Composite oxide and transistor

ABSTRACT

A novel material and a transistor using a novel material are provided. A composite oxide includes at least two regions, one of which includes In, Zn and an element M1 (the element M1 is one or more of Al, Ga, Si, B, Y, Ti, Fe, Ni, Ge, Zr, Mo, La, Ce, Nd, Hf, Ta, W, Mg, V, Be, and Cu), and the other of which includes In, Zn, and an element M2 (the element M2 is one or more of Al, Ga, Si, B, Y, Ti, Fe, Ni, Ge, Zr, Mo, La, Ce, Nd, Hf, Ta, W, Mg, V, Be, and Cu). The proportion of the element M1 to In, Zn, and the element M1 in the region including the element M1 is less than that of the element M2 to In, Zn, and the element M2 in the region including the element M2. In an analysis of the composite oxide by X-ray diffraction, the diffraction pattern result in the X-ray diffraction is asymmetric with the angle at which the peak intensity of X-ray diffraction is detected as the symmetry axis.

TECHNICAL FIELD

The present invention relates to an object, a method, or a manufacturing method. The present invention also relates to a process, a machine, manufacture, or a composition of matter. In particular, one embodiment of the present invention relates to a metal oxide or a manufacturing method of the metal oxide. One embodiment of the present invention also relates to a semiconductor device, a display device, a liquid crystal display device, a light-emitting device, a power storage device, a memory device, a method for driving them, or a method for manufacturing them.

In this specification and the like, a semiconductor device generally means a device that can function by utilizing semiconductor characteristics. A semiconductor element such as a transistor, a semiconductor circuit, an arithmetic device, and a memory device are each an embodiment of the semiconductor device. An imaging device, a display device, a liquid crystal display device, a light-emitting device, an electro-optical device, a power generation device, (including a thin film solar cell, an organic thin film solar cell, and the like), and an electronic device may each include a semiconductor device.

BACKGROUND ART

A technique in which a transistor is fabricated using an In—Ga—Zn-based metal oxide is disclosed (for example, see Patent Document 1).

Non-Patent Document 1 discusses a structure in which an active layer of a transistor includes two layers of metal oxides of an In—Zn oxide and an In—Ga—Zn oxide.

REFERENCES Patent Document

-   [Patent Document 1] Japanese Published Patent Application No.     2007-96055

Non-Patent Document

-   [Non-Patent Document 1] John F. Wager, “Oxide TFTs: A Progress     Report”, Information Display 1/16, SID 2016, January/February 2016,     Vol. 32, No. 1, pp. 16-21

SUMMARY OF THE INVENTION Problems to be Solved by the Invention

In Non-Patent Document 1, a channel-protective bottom-gate transistor includes a two-layer stack of indium zinc oxide and IGZO as an active layer and sets the thickness of the indium zinc oxide where a channel is formed to 10 nm, thereby achieving a high field-effect mobility (μ=62 cm²V⁻¹s⁻¹). However, the S value (the subthreshold swing, also referred to as SS), which is one of transistor characteristics, is as large as 0.41 V/decade. Moreover, the threshold voltage (Vth), which is also one of transistor characteristics, is −2.9 V, which means that the transistor has a normally-on characteristic.

In view of the above problems, an object of one embodiment of the present invention is to provide a novel metal oxide. Another object of one embodiment of the present invention is to give favorable electrical characteristics to a semiconductor device. Another object of one embodiment of the present invention is to provide a highly reliable semiconductor device. Another object of one embodiment of the present invention is to provide a semiconductor device with a novel structure. Another object of one embodiment of the present invention is to provide a display device with a novel structure.

Note that the description of these objects does not disturb the existence of other objects. In one embodiment of the present invention, there is no need to achieve all the objects. Other objects will be apparent from and can be derived from the description of the specification, the drawings, the claims, and the like.

Means for Solving the Problems

One embodiment of the present invention is a composite oxide including at least two regions. One of the regions includes In, Zn and an element M1 (the element M1 is one or more of Al, Ga, Si, B, Y, Ti, Fe, Ni, Ge, Zr, Mo, La, Ce, Nd, Hf, Ta, W, Mg, V, Be, and Cu), and the other region includes In, Zn, and an element M2 (the element M2 is one or more of Al, Ga, Si, B, Y, Ti, Fe, Ni, Ge, Zr, Mo, La, Ce, Nd, Hf, Ta, W, Mg, V, Be, and Cu). The proportion of the element M1 to In, Zn, and the element M1 in the region including the element M1 is less than the proportion of the element M2 to In, Zn, and the element M2 in the region including the element M2. In an analysis of the composite oxide by X-ray diffraction, the diffraction pattern result in the X-ray diffraction is asymmetric with the angle at which the peak intensity of X-ray diffraction is detected as the symmetry axis.

In the above embodiment, the peak intensity is detected between 2θ=30° and 2θ=35°.

In the above embodiment, the element M1 and the element M2 are Ga.

One embodiment of the present invention is a transistor including the above-described composite oxide, a gate, a source, and a drain. The composite oxide is used as a channel region in the transistor.

Effect of the Invention

According to one embodiment of the present invention, a novel metal oxide can be provided. According to another embodiment of the present invention, favorable electrical characteristics can be given to a semiconductor device. According to another embodiment of the present invention, a highly reliable semiconductor device can be provided. According to another embodiment of the present invention, a semiconductor device with a novel structure can be provided. According to another embodiment of the present invention, a display device with a novel structure can be provided.

Note that the description of these effects does not disturb the existence of other effects. One embodiment of the present invention does not necessarily achieve all the effects. Other effects will be apparent from and can be derived from the description of the specification, the drawings, the claims, and the like.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 A conceptual view of a composition of a metal oxide.

FIGS. 2A-2C Schematic views showing a transistor and distribution of energy levels in the transistor.

FIGS. 3A-3C Views showing a model of a schematic band diagram of a transistor.

FIGS. 4A-4C Views showing a model of a schematic band diagram of a transistor.

FIGS. 5A-5C Views showing a model of a schematic band diagram of a transistor.

FIGS. 6A-6C A top view and cross-sectional views showing a semiconductor device.

FIGS. 7A-7C A top view and cross-sectional views showing a semiconductor device.

FIGS. 8A-8B Cross-sectional views showing a semiconductor device.

FIGS. 9A-9D Cross-sectional views showing a method for manufacturing a semiconductor device.

FIGS. 10A-10C Cross-sectional views showing a method for manufacturing a semiconductor device;

FIGS. 11A-11C Cross-sectional views showing a method for manufacturing a semiconductor device.

FIGS. 12A-12C A top view and cross-sectional views showing a semiconductor device.

FIGS. 13A-13C A top view and cross-sectional views showing a semiconductor device.

FIGS. 14A-14C A top view and cross-sectional views showing a semiconductor device.

FIGS. 15A-15C A top view and cross-sectional views showing a semiconductor device.

FIGS. 16A-16C Views showing an atomic ratio range of a metal oxide of the present invention.

FIG. 17 A view showing a structure example of a display panel.

FIG. 18 A view showing a structure example of a display panel.

FIGS. 19A-19B Views showing a model of a metal oxide of one embodiment and its density of states.

FIGS. 20A-20D Views showing local structures of models of metal oxides to which impurities are added in one embodiment and their densities of states.

FIGS. 21A-21D Views showing local structures of models of metal oxides to which impurities are added in one embodiment and their densities of states.

FIGS. 22A-22D Views showing local structures of models of metal oxides to which impurities are added in one embodiment and their densities of states.

FIGS. 23A-23C Graphs showing the proportion of each kind of atoms obtained by using XPS measurement results of samples of Example.

FIG. 24 Graphs showing measured XRD spectra of samples of Example.

FIG. 25 A view showing an apparatus used for measurement of a sample of Example.

FIG. 26 A graph showing measured XRD spectra of samples of Example.

FIGS. 27A-27D Graphs showing measured XRD spectra of samples of Example.

FIGS. 28A-28D Graphs showing measured XRD spectra of samples of Example.

FIGS. 29A-29F Cross-sectional TEM images and electron diffraction patterns of samples of Example.

FIGS. 30A-30L A plan-view TEM image, a cross-sectional TEM image, and electron diffraction patterns of samples of Example.

FIG. 31 Plan-view TEM images of samples of Example and images obtained through analysis thereof.

FIGS. 32A-32D Views showing a method for deriving a rotation angle of a hexagon.

FIGS. 33A-33E Views showing a method for forming a Voronoi diagram.

FIG. 34 Graphs showing the numbers of shapes of Voronoi regions of Example and proportions thereof.

FIGS. 35A-35H Plan-view TEM images, cross-sectional TEM images, and EDX mapping images of samples of Example.

FIGS. 36A-36F EDX mapping images of samples of Example.

FIG. 37 Graphs showing I_(d)-V_(g) characteristics of samples of Example.

FIG. 38 Graphs showing I_(d)-V_(g) characteristics of samples after +GBT stress tests of Example.

FIGS. 39A-39B Graphs showing I_(d)-V_(g) characteristics and I_(d)-V_(d) characteristics of a transistor.

FIG. 40 A graph showing I_(d)-V_(g) characteristics and linear and saturation mobility curves which are calculated on the basis of GCA.

FIGS. 41A-41F Cross-sectional TEM images and electron diffraction patterns of samples of Example.

FIGS. 42A-42F Plan-view TEM images of samples of Example and images obtained through analysis thereof.

FIGS. 43A-43C Graphs showing the numbers of shapes of Voronoi regions of Example and proportions thereof.

FIGS. 44A-44H Plan-view TEM images, cross-sectional TEM images, and EDX mapping images of samples of Example.

FIGS. 45A-45C EDX mapping images of a sample of Example.

FIGS. 46A-46H Plan-view TEM images, cross-sectional TEM images, and EDX mapping images of samples of Example.

FIG. 47 Graphs showing I_(d)-V_(g) characteristics of samples of Example.

FIGS. 48A-48D A cross-sectional TEM image, EDX mapping images, and a graph showing an atomic ratio of a sample of Example.

FIGS. 49A-49D A plan-view TEM image, EDX mapping images, and a graph showing an atomic ratio of a sample of Example.

FIG. 50 A graph showing I_(d)-V_(g) characteristics.

FIG. 51 A graph showing I_(d)-V_(g) characteristics.

FIG. 52 A graph showing calculation results of a density of interface states.

FIGS. 53A-53B Graphs showing I_(d)-V_(g) characteristics.

FIG. 54 Graphs showing calculation results of a density of defect states.

FIG. 55 Graphs showing calculation results of a density of defect states.

FIG. 56 A graph showing I_(d)-V_(g) characteristics of a transistor.

MODE FOR CARRYING OUT THE INVENTION

Embodiments will be described below with reference to drawings. Note that embodiments can be carried out in many different modes, and it is easily understood by those skilled in the art that modes and details of the present invention can be modified in various ways without departing from the spirit and the scope of the present invention. Thus, the present invention should not be interpreted as being limited to the following description of the embodiments.

In the drawings, the size, the layer thickness, or the region is exaggerated for clarity in some cases. Therefore, the size, the layer thickness, or the region is not limited to the illustrated scale. Note that the drawings are schematic views showing ideal examples, and embodiments of the present invention are not limited to shapes, values, or the like shown in the drawings.

Note that in this specification, ordinal numbers such as “first”, “second”, and “third” are used in order to avoid confusion among components, and the terms do not limit the components numerically.

In this specification, terms for describing arrangement, such as “over” and “under”, are used for convenience in describing a positional relationship between components with reference to drawings. Furthermore, the positional relationship between components changes as appropriate in accordance with the direction in which each component is described. Thus, one embodiment of the present invention is not limited to terms used in this specification, and the terms can be changed appropriately depending on the situation.

In this specification and the like, a transistor is an element having at least three terminals of a gate, a drain, and a source. The transistor has a channel region between the drain (a drain terminal, a drain region, or a drain electrode) and the source (a source terminal, a source region, or a source electrode), and current can flow between the source and the drain through the channel region. Note that in this specification and the like, a channel region refers to a region through which current mainly flows.

Furthermore, functions of a source and a drain might be switched when a transistor of opposite polarity is employed or a direction of current flow is changed in circuit operation, for example. Therefore, the terms “source” and “drain” can be used interchangeably in this specification and the like.

In this specification and the like, the term “electrically connected” includes the case where components are connected through an “object having any electric function”. There is no particular limitation on an “object having any electric function” as long as electric signals can be transmitted and received between components that are connected through the object. Examples of the “object having any electric function” include a switching element such as a transistor, a resistor, an inductor, a capacitor, and an element with a variety of functions as well as an electrode and a wiring.

In this specification and the like, a silicon oxynitride film refers to a film that includes oxygen at a higher proportion than nitrogen, and a silicon nitride oxide film refers to a film that includes nitrogen at a higher proportion than oxygen.

In the description of components of the invention in this specification and the like with reference to the drawings, the same components in different drawings are denoted by the same reference numeral in some cases.

In this specification and the like, the term “parallel” indicates that the angle formed between two straight lines is greater than or equal to −10° and less than or equal to 10°. Thus, the case where the angle is greater than or equal to −5° and less than or equal to 5° is also included. In addition, the term “substantially parallel” indicates that the angle formed between two straight lines is greater than or equal to −30° and less than or equal to 30°. The term “perpendicular” indicates that the angle formed between two straight lines is greater than or equal to 80° and less than or equal to 100°. Thus, the case where the angle is greater than or equal to 85° and less than or equal to 95° is also included. In addition, the term “substantially perpendicular” indicates that the angle formed between two straight lines is greater than or equal to 60° and less than or equal to 120°.

In this specification and the like, the terms “film” and “layer” can be interchanged with each other depending on the case. For example, the term “conductive layer” can be changed into the term “conductive film” in some cases. Also, for example, the term “insulating film” can be changed into the term “insulating layer” in some cases.

Note that a “semiconductor” includes characteristics of an “insulator” in some cases when the conductivity is sufficiently low, for example. Furthermore, a “semiconductor” and an “insulator” cannot be strictly distinguished from each other in some cases because a border therebetween is not clear. Accordingly, a “semiconductor” described in this specification can be called an “insulator” in some cases. Similarly, an “insulator” described in this specification can be called a “semiconductor” in some cases.

Note that in this specification and the like, In:Ga:Zn=4:2:3 or a neighborhood of In; Ga:Zn=4:2:3 refers to an atomic ratio where, when In is 4 with respect to the total number of atoms, Ga is greater than or equal to 1 and less than or equal to 3 (1≤Ga≤3) and Zn is greater than or equal to 2 and less than or equal to 4 (2≤Zn≤4). In:Ga:Zn=5:1:6 or a neighborhood of In:Ga:Zn=5:1:6 refers to an atomic ratio where, when In is 5 with respect to the total number of atoms, Ga is greater than 0.1 and less than or equal to 2 (0.1<Ga≤2) and Zn is greater than or equal to 5 and less than or equal to 7 (5≤Zn≤7). In:Ga:Zn=1:1:1 or a neighborhood of In; Ga:Zn=1:1:1 refers to an atomic ratio where, when In is 1 with respect to the total number of atoms, Ga is greater than 0.1 and less than or equal to 2 (0.1<Ga≤2) and Zn is greater than 0.1 and less than or equal to 2 (0.1<Zn≤2).

Embodiment 1

In this embodiment, a composite oxide of one embodiment of the present invention will be described. Note that the composite oxide is an oxide having a cloud-aligned composite (CAC) composition. Examples of the composite oxide include a metal oxide containing a plurality of metal elements.

In this specification, the composite oxide which is one embodiment of the present invention is defined as a CAC-OS (oxide semiconductor) when having a semiconductor function.

The CAC-OS or the CAC-metal oxide is referred to as a matrix composite or a metal matrix composite in some cases.

The composite oxide of one embodiment of the present invention preferably contains at least indium. In particular, indium and zinc are preferably contained. In addition, an element M (the element M is one or more elements selected from aluminum, gallium, yttrium, copper, vanadium, beryllium, boron, silicon, titanium, iron, nickel, germanium, zirconium, molybdenum, lanthanum, cerium, neodymium, hafnium, tantalum, tungsten, magnesium, and the like) may be contained.

The composite oxide of one embodiment of the present invention preferably contains nitrogen. Specifically, the nitrogen concentration in the composite oxide of one embodiment of the present invention measured by SIMS may be 1×10¹⁶ atoms/cm³ or higher, preferably 1×10¹⁷ atoms/cm³ or higher and 2×10²² atoms/cm³ or lower. Note that a composite oxide to which nitrogen is added tends to have a smaller band gap and thus have improved conductivity. Thus, in this specification and the like, the composite oxide of one embodiment of the present invention includes a composite oxide to which nitrogen or the like is added. Moreover, a composite oxide containing nitrogen may be referred to as a composite oxynitride (metal oxynitride).

Here, the case where the composite oxide contains indium, the element M, and zinc is considered. The terms of the atomic ratio of indium to the element M and zinc contained in the composite oxide are denoted by [In], [M], and [Zn], respectively.

<Composition of Composite Oxide>

A conceptual view of a metal oxide which is a composite oxide having a CAC composition of the present invention is illustrated in FIG. 1 .

For example, in the CAC-OS, as illustrated in FIG. 1 , elements constituting a metal oxide are unevenly distributed over a substrate (described as Sub. in FIG. 1 ), and regions 001 mainly including an element and regions 002 mainly including another element are formed. The regions 001 and 002 are mixed to form a mosaic pattern. In other words, the CAC-OS has a composition of a material in which elements constituting the metal oxide are unevenly distributed with a size greater than or equal to 0.5 nm and less than or equal to 10 nm, preferably less than or equal to 3 nm, or a similar size. Note that in the following description, a mosaic pattern or a patch-like pattern of a metal oxide refers to a state in which one or more metal elements are unevenly distributed and regions which include the metal element and each have a size of greater than or equal to 0.5 nm and less than or equal to 10 nm, preferably less than or equal to 3 nm, or a similar size are mixed.

For example, an In-M-Zn oxide with the CAC composition has a composition in which materials are separated into an indium oxide (hereinafter referred to as InO_(X1) (X1 is a real number greater than 0)) or an indium zinc oxide (hereinafter referred to as In_(X2)Zn_(Y2)O_(Z2) (X2, Y2, and Z2 are real numbers greater than 0)), an oxide including the element M, and the like, and thus a mosaic pattern is formed. In the composition, InO_(X1) or In_(X2)Zn_(Y2)O_(Z2) forming the mosaic pattern is distributed in the film (hereinafter also referred to as a cloud-like composition). Note that in this specification, a slight amount of gallium (Ga) may be mixed in the separated InO_(X1) or In_(X2)Zn_(Y2)O_(Z2) so that a solid solution state is formed.

In other words, the metal oxide of one embodiment of the present invention includes at least two or more oxides or materials selected from an In oxide, an In-M oxide, an M oxide, an M-Zn oxide, an In—Zn oxide, and an In-M-Zn oxide.

Typically, the metal oxide of one embodiment of the present invention includes at least two or more oxides selected from an In oxide, an In—Zn oxide, an In—Al—Zn oxide, an In—Ga—Zn oxide, an In—Y—Zn oxide, an In—Cu—Zn oxide, an In—V—Zn oxide, an In—Be—Zn oxide, an In—B—Zn oxide, an In—Si—Zn oxide, an In—Ti—Zn oxide, an In—Fe—Zn oxide, an In—Ni—Zn oxide, an In—Ge—Zn oxide, an In—Zr—Zn oxide, an In—Mo—Zn oxide, an In—La—Zn oxide, an In—Ce—Zn oxide, an In—Nd—Zn oxide, an In—Hf—Zn oxide, an In—Ta—Zn oxide, an In—W—Zn oxide, and an In—Mg—Zn oxide. That is, the metal oxide of one embodiment of the present invention can be referred to as a composite metal oxide including a plurality of materials or a plurality of components.

Here, let a concept in FIG. 1 illustrate an In-M-Zn oxide with the CAC composition. In this case, it can be said that the region 001 is a region including an oxide including the element M as a main component and the region 002 is a region including In_(X2)Zn_(Y2)O_(Z2) or InO_(X1) as a main component. At this time, surrounding portions of the region including an oxide including the element M as a main component, the region including In_(X2)Zn_(Y2)O_(Z2) or InO_(X1) as a main component, and a region including at least Zn are unclear (blurred), so that boundaries are not clearly observed in some cases.

In other words, an In-M-Zn oxide with the CAC composition is a metal oxide in which a region including an oxide including the element M as a main component and a region including In_(X2)Zn_(Y2)O_(Z2) or InO_(X1) as a main component are mixed. Accordingly, the metal oxide is referred to as a composite metal oxide in some cases. Note that in this specification, for example, when the atomic ratio of In to the element M in the region 002 is greater than the atomic ratio of In to the element M in the region 001, the region 002 has higher In concentration than the region 001.

Note that in the metal oxide having the CAC composition, a stacked-layer structure including two or more kinds of films with different compositions is not included. For example, a two-layer structure of a film including In as a main component and a film including Ga as a main component is not included.

Specifically, a CAC-OS in an In—Ga—Zn oxide (an In—Ga—Zn oxide in the CAC-OS may be particularly referred to as CAC-IGZO) is described. In the CAC-OS in the In—Ga—Zn oxide, materials are separated into InO_(X1) or In_(X2)Zn_(Y2)O_(Z2) and an oxide including gallium, for example, and a mosaic pattern is formed. InO_(X1) or In_(X2)Zn_(Y2)O_(Z2) with the mosaic pattern is a cloud-like metal oxide.

In other words, the CAC-OS in the In—Ga—Zn oxide is a composite metal oxide having a composition in which a region including an oxide including gallium as a main component and a region including In_(X2)Zn_(Y2)O_(Z2) or InO_(X1) as a main component are mixed. Surrounding portions of the region including an oxide including gallium as a main component and the region including In_(X2)Zn_(Y2)O_(Z2) or InO_(X1) as a main component are unclear (blurred), so that boundaries are not clearly observed in some cases.

For example, in the conceptual view in FIG. 1 , the region 001 corresponds to the region including an oxide including gallium as a main component and the region 002 corresponds to the region including In_(X2)Zn_(Y2)O_(Z2) or InO_(X1) as a main component. The region including an oxide including gallium as a main component and the region including In_(X2)Zn_(Y2)O_(Z2) or InO_(X1) as a main component may each be referred to as a nanoparticle. The diameter of the nanoparticle is greater than or equal to 0.5 nm and less than or equal to 10 nm, typically greater than or equal to 1 nm and less than or equal to 2 nm. Surrounding portions of the nanoparticles are unclear (blurred), so that a boundary is not clearly observed in some cases.

Note that the sizes of the region 001 and the region 002 can be evaluated with energy dispersive X-ray spectroscopy EDX mapping obtained by EDX. For example, the diameter of the region 001 is observed to be greater than or equal to 0.5 nm and less than or equal to 10 nm, or less than or equal to 3 nm in the EDX mapping of a cross-sectional photograph in some cases. The density of an element that is a main component is gradually lowered from the central portion of the region toward the surrounding portion. For example, when the concentration of the element (hereinafter also referred to as abundance) in an EDX mapping gradually decreases from the central portion toward the surrounding portion, the surrounding portion of the region is indistinct (unclear (blurred)) in observation of the EDX mapping of the cross-sectional photograph. For example, from the central portion toward the surrounding portion in the region including InO_(X1) as a main component, the number of In atoms gradually reduces and the number of Zn atoms increases, so that the region gradually changes into the region including In_(X2)Zn_(Y2)O_(Z2) as a main component. Thus, the surrounding portion of the region including GaO_(X3) as a main component is indistinct in observation of the EDX mapping.

For this reason, when [In] in the region 001 or the region 002 included in the In—Ga—Zn oxide is 1, [Ga] and [Zn] are not limited to integers. That is, since surrounding portions of the region 001 and the region 002 are unclear and concentration distributions of the metal elements are generated in the region 001 and the region 002, [Ga] and [Zn] are not necessarily integers when [In] is 1. Thus, even in the In—Ga—Zn oxide including the region 001 and the region 002, [Ga] and [Zn] are not limited to integers when [In] is 1.

Here, in the case where an In-M-Zn oxide can be represented in the form of InM_(m)Zn_(n)O_(p), for example, the region 001 included in the composite oxide of one embodiment of the present invention can be represented as InM_(m1)Zn_(n1)O_(p1). Similarly, the region 002 included in the composite oxide of one embodiment of the present invention can be represented as InM_(m2)Zn_(n2)O_(p2). Note that m, n, p, m1, n1, p1, m2, n2, and p2 described above are each an integer or a non-integer.

In this specification and the like, the In-M-Zn oxide represented as InM_(m)Zn_(n)O_(p), InM_(m1)Zn_(n1)O_(p1), or InM_(m2)Zn_(n2)O_(p2) is referred to as InMZnO-based oxide in some cases. In the stoichiometric proportion of InMZnO-based oxide, when In is 1, each of M and Zn is an integer or a non-integer. Note that the case where the value of the stoichiometric composition is varied between portions in the region is included.

A crystal structure of the In—Ga—Zn oxide with the CAC composition is not particularly limited. The region 001 and the region 002 may have different crystal structures.

Here, an In—Ga—Zn—O-based metal oxide is referred to as IGZO in some cases. IGZO is a commonly known name and sometimes refers to one compound formed of In, Ga, Zn, and O.

A crystalline compound can be given as an example of the In—Ga—Zn—O-based metal oxide. The crystalline compound has a single crystal structure, a polycrystalline structure, or a c-axis aligned crystalline (CAAC) structure. Note that the CAAC structure is a layered crystal structure in which a plurality of IGZO nanocrystals have c-axis alignment and are connected in the a-b plane without alignment.

In contrast, of the CAC-OS in the In—Ga—Zn oxide, the crystal structure is a secondary element. In this specification, CAC-IGZO can be defined as a metal oxide including In, Ga, Zn, and O in the state where a plurality of regions including Ga as a main component and a plurality of regions including In as a main component are each dispersed randomly forming a mosaic pattern.

For example, in the conceptual view in FIG. 1 , the region 001 corresponds to the region including Ga as a main component and the region 002 corresponds to the region including In as a main component. The region including Ga as a main component and the region including In as a main component may each be referred to as a nanoparticle. The diameter of the nanoparticle is greater than or equal to 0.5 nm and less than or equal to 10 nm, typically less than or equal to 3 nm. Surrounding portions of the nanoparticles are unclear (blurred), so that a boundary is not clearly observed in some cases.

Note that the crystallinity of the CAC-OS in an In—Ga—Zn oxide can be analyzed by electron diffraction. For example, a ring-like region with high luminance is observed in an electron diffraction pattern image. Furthermore, a plurality of spots are observed in the ring-shaped region in some cases.

As described above, the CAC-OS in the In—Ga—Zn oxide has a structure different from that of an IGZO compound in which metal elements are evenly distributed, and has properties different from those of the IGZO compound. That is, in the CAC-OS in the In—Ga—Zn oxide, regions including an oxide including gallium or the like as a main component and regions including In_(X2)Zn_(Y2)O_(Z2) or InO_(X1) as a main component are separated from each other, and the regions including the respective elements as the main components form a mosaic pattern.

The region including In_(X2)Zn_(Y2)O_(Z2) or InO_(X1) as a main component is a region whose conductivity is higher than that of the region including an oxide including gallium or the like as a main component. In other words, when carriers flow through the regions including In_(X2)Zn_(Y2)O_(Z2) or InO_(X1) as a main component, the conductivity of an oxide semiconductor is exhibited. Accordingly, when the regions including In_(X2)Zn_(Y2)O_(Z2) or InO_(X1) as a main component are distributed in an oxide semiconductor like a cloud, high field-effect mobility (μ) can be achieved. Note that the region including In_(X2)Zn_(Y2)O_(Z2) or InO_(X1) as a main component can be said to be a semiconductor region whose properties are close to those of a conductor.

In contrast, the region including an oxide including gallium or the like as a main component is a region whose insulating property is higher than that of the region including In_(X2)Zn_(Y2)O_(Z2) or InO_(X1) as a main component. In other words, when the regions including an oxide including gallium or the like as a main component are distributed in an oxide semiconductor, leakage current can be suppressed and favorable switching operation can be achieved. Note that the region including In_(a)Ga_(b)Zn_(c)O_(d) or the like as a main component can be said to be a semiconductor region whose properties are close to those of an insulator.

Accordingly, when the CAC-OS in the In—Ga—Zn oxide is used for a semiconductor element, the insulating property derived from the oxide including gallium or the like and the conductivity derived from In_(X2)Zn_(Y2)O_(Z2) or InO_(X1) complement each other, whereby high on-state current (I_(on)), high field-effect mobility (μ), and low off-state current (I_(off)) can be achieved.

A semiconductor element that includes a CAC-OS in an In—Ga—Zn oxide has high reliability. Thus, the CAC-OS in the In—Ga—Zn oxide is the most suitable for a variety of semiconductor devices typified by a display.

<Transistor Including Metal Oxide>

Next, the case where the metal oxide is used as a semiconductor in a transistor is described.

Note that with the use of the metal oxide as a semiconductor in a transistor, the transistor having high field-effect mobility and high switching characteristics can be achieved. In addition, the transistor having high reliability can be achieved.

FIG. 2(A) is a schematic view of a transistor including the metal oxide in a channel region. The transistor in FIG. 2(A) includes a source, a drain, a first gate, a second gate, a first gate insulating portion (GI1), a second gate insulating portion (GI2), and a channel. The resistance of the channel of the transistor can be controlled by a potential applied to the gate. That is, conduction (the on state of the transistor) or non-conduction (the off state of the transistor) between the source and the drain can be controlled by a potential applied to the first gate or the second gate.

The channel includes a CAC-OS in which the regions 001 having a first band gap and the regions 002 having a second band gap are distributed like a cloud. Note that the first band gap is larger than the second band gap. Thus, in this specification, the first band gap is denoted as wide Eg, Eg001, or the like, in some cases. The second band gap is denoted as narrow Eg, Eg002, or the like, in some cases.

For example, the case where the In—Ga—Zn oxide with the CAC composition is used as the CAC-OS in the channel is described. The In—Ga—Zn oxide with the CAC composition has a (cloud-like) composition in which materials are separated into, as the region 001, a region including In_(a)Ga_(b)Zn_(c)O_(d) as a main component and having higher Ga concentration than the region 002, and, as the region 002, a region including In_(X2)Zn_(Y2)O_(Z2) or InO_(X1) as a main component and having higher In concentration than the region 001 and form a mosaic pattern, and In_(a)Ga_(b)Zn_(c)O_(d), and InO_(X1) or In_(X2)Zn_(Y2)O_(Z2) are distributed in the film. Note that the region 001 including In_(a)Ga_(b)Zn_(c)O_(d) as a main component has a band gap larger than that of the region 002 including In_(X2)Zn_(Y2)O_(Z2) or InO_(X1) as a main component.

A conduction model of the transistor illustrated in FIG. 2(A), which includes the CAC-OS in the channel, is described. FIG. 2(B) is a schematic view showing distribution of energy levels between the source and the drain of the transistor illustrated in FIG. 2(A). FIG. 2(C) is a conduction band diagram on solid line X-X′ in the transistor illustrated in FIG. 2(A). Note that in each conduction band diagram, a solid line indicates the energy of the conduction band minimum. A dashed-dotted line represented by E_(f) indicates the energy of the quasi-Fermi level of electrons. Here, a negative voltage is applied between the gate and the source as a first gate voltage and a drain voltage (V_(d)>0) is applied between the source and the drain.

When a negative gate voltage is applied to the transistor illustrated in FIG. 2(A), an energy of a conduction band minimum CB₀₀₁ derived from the region 001 and an energy of a conduction band minimum CB₀₀₂ derived from the region 002 are formed between the source and the drain as illustrated in FIG. 2(B). Since the first band gap is larger than the second band gap, the potential barrier of the energy of the conduction band minimum CB₀₀₁ is higher than the potential barrier of the energy of the conduction band minimum CB₀₀₂. That is, the maximum value of the potential barrier in the channel is a value derived from the region 001. Thus, the use of the CAC-OS in the channel can suppress leakage current and achieve a transistor having high switching characteristics.

As illustrated in FIG. 2(C), the band gap of the region 001 having the first band gap is relatively wider than the band gap of the region 002 having the second band gap; thus, the energy level of the conductive band minimum (the Ec edge) derived from the region 001 having the first band gap can exist at a relatively higher level than the energy level of the conductive band minimum (the Ec edge) derived from the region 002 having the second band gap.

For example, it is assumed that a component of the region 001 having the first band gap is an In—Ga—Zn oxide (In:Ga:Zn=1:1:1 [atomic ratio]), and a component of the region 002 having the second band gap is an In—Zn oxide (In:Zn=2:3 [atomic ratio]). In this case, the first band gap is 3.3 eV or a value in the vicinity thereof, and the second band gap is 2.4 eV or a value in the vicinity thereof. Note that values obtained by measurement of single films of respective materials with an ellipsometer are used as the values of the band gaps.

In the above assumption, the difference between the first band gap and the second band gap is 0.9 eV. In one embodiment of the present invention, the difference between the first band gap and the second band gap is at least 0.1 eV or more. Note that the level of the valence band maximum derived from the region 001 having the first band gap is different from the level of the valence band maximum derived from the region 002 having the second band gap in some cases; thus, the difference between the first band gap and the second band gap is preferably 0.3 eV or more, further preferably 0.4 eV or more.

In the above assumption, carriers flow through the CAC-OS owing to an In—Zn oxide which has the second band gap, i.e., a narrow band gap. At this time, the carriers overflow from the second band gap into the In—Ga—Zn oxide side which has the first band gap, i.e., a wide band gap. In other words, carriers are more easily generated in an In—Zn oxide which has a narrow band gap, and the carriers move to an In—Ga—Zn oxide which has a wide band gap.

Note that in the metal oxide where the channel is formed, the regions 001 and the regions 002 form a mosaic pattern and the regions 001 and the regions 002 are irregularly unevenly distributed. For this reason, the conduction band diagram on solid line X-X′ is merely an example.

It is basically acceptable as long as a band in which the region 002 is between the regions 001 is formed as shown in FIG. 3(A). Alternatively, it is acceptable as long as a band in which the region 001 is between the regions 002 is formed.

In a connection portion of the region 001 having the first band gap and the region 002 having the second band gap in the actual CAC-OS, an aggregation state and the composition of the regions probably become unstable. Accordingly, as illustrated in FIG. 3(B) and FIG. 3(C), the bands change not discontinuously but continuously in some cases. In other words, the first band gap and the second band gap work together when carriers flow through the CAC-OS.

FIG. 4 shows a model of a schematic band diagram of the transistor in the direction along X-X′ in FIG. 2(A), which corresponds to the schematic view in FIG. 2(B). Note that when a voltage is applied to the first gate, the same voltage is simultaneously applied to the second gate. FIG. 4(A) shows a state (ON State) in which, as a first gate voltage V_(g), a positive voltage (V_(g)>0) is applied between each of the gates and the source. FIG. 4(B) shows a state in which the first gate voltage V_(g) is not applied (V_(g)=0). FIG. 4(C) shows a state (OFF State) in which, as the first gate voltage V_(g), a negative voltage (V_(g)<0) is applied between each of the gates and the source. Note that in the channel, a dashed line indicates the energy of the conduction band minimum in the case where no voltage is applied, and a solid line indicates the energy of the conduction band minimum in the case where a voltage is applied. A dashed-dotted line represented by E_(f) indicates the energy of the quasi-Fermi level of electrons.

In a transistor including the CAC-OS in a channel, the region 001 having the first band gap and the region 002 having the second band gap electrically interact with each other. In other words, the region 001 having the first band gap and the region 002 having the second band gap function complementarily.

In other words, in the case where a forward voltage is applied as shown in FIG. 4(A), the conduction band of the region 001 becomes lower than the conduction band of the region 002. Accordingly, carriers flow in not only the conduction band of the region 002 but also the conduction band of the region 001, so that a high on-state current can be obtained. Meanwhile, in the case where a reverse voltage is applied as shown in FIG. 4(B) and FIG. 4(C), the conduction bands of the region 001 and the region 002 become higher, which probably causes a significant reduction in the current flowing between the source and the drain.

FIG. 5 shows a model of a schematic band diagram of the transistor on solid line X-X′ in FIG. 2(A), which corresponds to the schematic view in FIG. 2(C). Note that when a voltage is applied to the first gate, the same voltage is simultaneously applied to the second gate. FIG. 5(A) shows a state (ON State) in which, as the first gate voltage V_(g), a positive voltage (V_(g)>0) is applied between each of the gates and the source. FIG. 5(B) shows a state in which the first gate voltage V_(g) is not applied (V_(g)=0). FIG. 5(C) shows a state (OFF State) in which, as the first gate voltage V_(g), a negative voltage (V_(g)<0) is applied between each of the gates and the source. Note that in the channel, a solid line indicates the energy of the conduction band minimum. The dashed-dotted line represented by E_(f) indicates the energy of the quasi-Fermi level of electrons. Here, the energy difference between the conduction band minimum of the region 001 and the conduction band minimum of the region 002 is represented as ΔEc. Furthermore, ΔEc (V_(g)=0) indicates ΔEc in a state where a voltage is not applied (V_(g)=0), ΔEc (V_(g)>0) indicates ΔEc in a state where a voltage at which the transistor is turned on (V_(g)>0) is applied, and ΔEc (V_(g)<0) indicates ΔEc in a state where a negative voltage (V_(g)<0) is applied.

As illustrated in FIG. 5(A), when a potential at which the transistor is turned on (V_(g)>0) is applied to the first gate, ΔEc (V_(g)>0)<ΔEc (V_(g)=0) is satisfied. Thus, electrons flow in the region 002 having the second band gap with the low energy level of the conductive band minimum (the Ec edge) and serving as a main conduction path; at the same time, electrons also flow in the region 001 having the first band gap. Therefore, high current drive capability in the on state of the transistor, i.e., high on-state current and high field-effect mobility can be obtained.

In contrast, as illustrated in FIG. 5(B) and FIG. 5(C), when a voltage lower than the threshold voltage (V_(g)≤0) is applied to the first gate, the region 001 having the first band gap serves as a dielectric (insulator), so that the conduction path in the region 001 is blocked. The region 002 having the second band gap is in contact with the region 001 having the first band gap. Consequently, the region 001 having the first band gap electrically interacts with itself and also with the region 002 having the second band gap, and thus, even the conduction path in the region 002 having the second band gap is blocked. Accordingly, the whole channel is brought into a non-conductive state, and the transistor is turned off. Therefore, ΔEc (V_(g)=0)<ΔEc (V_(g)<0) is satisfied.

As described above, with the use of the CAC-OS in a transistor, it is possible to reduce or prevent leakage current between a gate and a source or a drain, which is generated when the transistor operates, for example, when a potential difference is generated between the gate and the source or the drain.

A semiconductor with a low carrier density is preferably used in a transistor. A highly purified intrinsic or substantially highly purified intrinsic metal oxide has few carrier generation sources and thus can have a low carrier density. The highly purified intrinsic or substantially highly purified intrinsic metal oxide has a low density of defect states and accordingly has a low density of trap states in some cases.

Charge trapped by the trap states in the metal oxide takes a long time to be released and may behave like fixed charge. Thus, a transistor whose channel region is formed in a metal oxide having a high density of trap states has unstable electrical characteristics in some cases.

Accordingly, in order to obtain stable electrical characteristics of the transistor, it is effective to reduce the concentration of impurities in the metal oxide. In addition, in order to reduce the concentration of impurities in the metal oxide, the concentration of impurities in an adjacent film is also preferably reduced. Examples of impurities include hydrogen, alkali metal, alkaline earth metal, iron, nickel, and silicon.

Here, the influence of each impurity in the metal oxide will be described.

When silicon or carbon that is a Group 14 element is contained in the metal oxide, defect states are formed in the metal oxide. Thus, the concentration of silicon or carbon in the metal oxide and the concentration of silicon or carbon around an interface with the metal oxide (the concentration measured by secondary ion mass spectrometry SIMS) is set to be lower than or equal to 2×10¹⁸ atoms/cm³, preferably lower than or equal to 2×10¹⁷ atoms/cm³.

When the metal oxide contains an alkali metal or an alkaline earth metal, defect states are formed and carriers are generated, in some cases. Thus, a transistor including a metal oxide that contains an alkali metal or an alkaline earth metal is likely to be normally on. Therefore, it is preferable to reduce the concentration of an alkali metal or an alkaline earth metal in the metal oxide. Specifically, the concentration of an alkali metal or an alkaline earth metal in the metal oxide measured by SIMS is set to be lower than or equal to 1×10¹⁸ atoms/cm³, preferably lower than or equal to 2×10¹⁶ atoms/cm³.

Hydrogen included in the metal oxide reacts with oxygen bonded to a metal atom to be water, and thus causes an oxygen vacancy (Vo) in some cases. Due to entry of hydrogen into the oxygen vacancy (Vo), an electron serving as a carrier is generated in some cases. Furthermore, in some cases, bonding of part of hydrogen to oxygen bonded to a metal atom generates an electron serving as a carrier. Thus, a transistor including the metal oxide that includes hydrogen is likely to be normally on. Accordingly, hydrogen in the metal oxide is preferably reduced as much as possible. Specifically, the hydrogen concentration of the metal oxide, which is measured by SIMS, is set to be lower than 1×10²⁰ atoms/cm³, preferably lower than 1×10¹⁹ atoms/cm³, further preferably lower than 5×10¹⁸ atoms/cm³, still further preferably lower than 1×10¹⁸ atoms/cm³.

Note that the oxygen vacancies (Vo) in the metal oxide can be reduced by introduction of oxygen into the metal oxide. That is, the oxygen vacancies (Vo) in the metal oxide disappear when the oxygen vacancies (Vo) are filled with oxygen. Accordingly, diffusion of oxygen in the metal oxide can reduce the oxygen vacancies (Vo) in a transistor and improve the reliability.

Note that as a method for introducing oxygen into the metal oxide, for example, an oxide in which oxygen content is higher than the oxygen content in the stoichiometric composition can be provided in contact with the metal oxide. That is, in the oxide, a region including oxygen in excess of that in the stoichiometric composition (hereinafter also referred to as an excess oxygen region) is preferably formed. In particular, in the case of using a metal oxide in a transistor, an oxide including an excess oxygen region is provided in a base film, an interlayer film, or the like in the vicinity of the transistor, whereby oxygen vacancies in the transistor are reduced, and the reliability can be improved.

When a metal oxide in which impurities are sufficiently reduced is used for a channel formation region in a transistor, stable electrical characteristics can be obtained.

<Method for Forming Metal Oxide Film>

An example of a method for forming the metal oxide film is described below.

The metal oxide film is preferably formed at a temperature higher than or equal to room temperature and lower than 140° C. Note that room temperature includes not only the case where temperature control is not performed but also the case where temperature control is performed, e.g., the case where a substrate is cooled.

As a sputtering gas, a rare gas (typically argon), oxygen, or a mixed gas of a rare gas and oxygen is used as appropriate. In the case of the mixed gas, the proportion of the oxygen gas in the whole film formation gas is higher than or equal to 0% and lower than or equal to 30%, preferably higher than or equal to 5% and lower than or equal to 20%.

Note that when the sputtering gas contains oxygen, oxygen can be added to a film under the metal oxide and an excess oxygen region can be provided at the same time as the formation of the metal oxide film. In addition, increasing the purity of a sputtering gas is necessary. For example, as an oxygen gas or an argon gas used for a sputtering gas, a gas highly purified to have a dew point of −40° C. or lower, preferably −80° C. or lower, further preferably −100° C. or lower, still further preferably −120° C. or lower is used, whereby entry of moisture or the like into the metal oxide can be prevented as much as possible.

In the case where the metal oxide film is formed by a sputtering method, a chamber in a sputtering apparatus is preferably evacuated to a high vacuum (to the degree of approximately 5×10⁻⁷ Pa to 1×10⁻⁴ Pa) with an adsorption vacuum pump such as a cryopump in order to remove as much water as possible or the like, which serves as an impurity for the metal oxide. Alternatively, a turbo molecular pump and a cold trap are preferably combined so as to prevent a backflow of a gas, especially a gas containing carbon or hydrogen from an exhaust system to the inside of the chamber.

As a target, an In—Ga—Zn metal oxide target can be used. For example, a metal oxide target having [In]:[Ga]:[Zn]=4:2:4.1 [atomic ratio], [In]:[Ga]:[Zn]=5:1:7 [atomic ratio], or the atomic ratio in the neighborhood thereof is preferably used.

In the sputtering apparatus, the target may be rotated or moved. For example, the magnet unit is oscillated vertically and/or horizontally during the film formation, whereby the composite metal oxide of the present invention can be formed. For example, the target may be rotated or oscillated with a beat (also referred to as rhythm, beat, pulse, frequency, period, cycle, or the like) of greater than or equal to 0.1 Hz and less than or equal to 1 kHz. Alternatively, the magnet unit may be oscillated with a beat of greater than or equal to 0.1 Hz and less than or equal to 1 kHz.

The metal oxide of the present invention can be formed, for example, by using a mixed gas of oxygen and a rare gas in which the proportion of oxygen is approximately 10% as a sputtering gas; setting the substrate temperature to 130° C.; and oscillating an In—Ga—Zn metal oxide target having [In]:[Ga]:[Zn]=4:2:4.1 [atomic ratio] during the film formation.

The structure described in this embodiment can be used in combination with any of the structures described in the other embodiments or the other examples as appropriate.

Embodiment 2

In this embodiment, semiconductor devices of one embodiment of the present invention, and manufacturing methods thereof will be described with reference to FIG. 6 to FIG. 15 .

2-1. Structure Example 1 of Semiconductor Device

FIG. 6(A) is a top view of a transistor 100 that is a semiconductor device of one embodiment of the present invention; FIG. 6(B) corresponds to a cross-sectional view of a cross section taken along dashed-dotted line X1-X2 in FIG. 6(A); and FIG. 6(C) corresponds to a cross-sectional view of a cross section taken along dashed-dotted line Y1-Y2 in FIG. 6(A). Note that in FIG. 6(A), some components of the transistor 100 (e.g., an insulating film functioning as a gate insulating film) are not illustrated to avoid complexity. The direction of the dashed-dotted line X1-X2 may be called a channel length direction, and the direction of the dashed-dotted line Y1-Y2 may be called a channel width direction. Note that as in FIG. 6(A), some components are not illustrated in some cases in top views of transistors in the following drawings.

The transistor 100 illustrated in FIGS. 6(A), 6(B), and 6(C) is what is called a top-gate transistor.

The transistor 100 includes an insulating film 104 over a substrate 102, a metal oxide 108 over the insulating film 104, an insulating film 110 over the metal oxide 108, a conductive film 112 over the insulating film 110, and an insulating film 116 over the insulating film 104, the metal oxide 108, and the conductive film 112.

The metal oxide 108 includes a region overlapping with the conductive film 112 with the insulating film 110 interposed therebetween. For example, the metal oxide 108 preferably contains In, M (M is Al, Ga, Y, or Sn), and Zn.

The metal oxide 108 includes regions 108 n in regions which do not overlap with the conductive film 112 and are in contact with the insulating film 116. The regions 108 n are n-type regions in the metal oxide 108 described above. Note that the regions 108 n are in contact with the insulating film 116, and the insulating film 116 contains nitrogen or hydrogen. Accordingly, nitrogen or hydrogen in the insulating film 116 is added to the regions 108 n to increase the carrier density, thereby making the regions 108 n n-type.

The metal oxide 108 preferably includes a region in which the atomic proportion of In is larger than the atomic proportion of M. For example, the atomic ratio of In to M and Zn in the metal oxide 108 is preferably In:M:Zn=4:2:3 or in the neighborhood thereof.

Note that the composition of the metal oxide 108 is not limited to the above. For example, the atomic ratio of In to M and Zn in the metal oxide 108 may be In:M:Zn=5:1:6 or in the neighborhood thereof. The term “neighborhood” includes the following: when In is 5, M is greater than or equal to 0.5 and less than or equal to 1.5, and Zn is greater than or equal to 5 and less than or equal to 7.

When the metal oxide 108 has a region in which the atomic proportion of In is larger than the atomic proportion of M, the transistor 100 can have high field-effect mobility. Specifically, the field-effect mobility of the transistor 100 can exceed 10 cm²/Vs, preferably exceed 30 cm²/Vs.

For example, with the use of the transistor with high field-effect mobility in a gate driver that generates a gate signal, the display device with a small frame width (also referred to as a narrow frame) can be provided. Furthermore, with the use of the above transistor with high field-effect mobility in a source driver included in a display device (particularly a demultiplexer connected to an output terminal of a shift register included in the source driver), a display device to which fewer wirings are connected can be provided.

Meanwhile, even when the metal oxide 108 includes a region in which the atomic proportion of In is larger than the atomic proportion of M, the field-effect mobility might be low if the metal oxide 108 has high crystallinity.

Note that the crystallinity of the metal oxide 108 can be determined by analysis by XRD (X-Ray Diffraction) or with a transmission electron microscope (TEM), for example.

First, oxygen vacancies that might be formed in the metal oxide 108 will be described.

Oxygen vacancies formed in the metal oxide 108 adversely affect the transistor characteristics and therefore cause a problem. For example, when oxygen vacancies are formed in the metal oxide 108, hydrogen is bonded to the oxygen vacancies to serve as a carrier supply source. The carrier supply source generated in the metal oxide 108 causes a change in the electrical characteristics, typically, a shift in the threshold voltage, of the transistor 100 including the metal oxide 108. Therefore, it is preferable that the amount of oxygen vacancies in the metal oxide 108 be as small as possible.

In view of the above, one embodiment of the present invention employs a structure in which the insulating film in the vicinity of the metal oxide 108, specifically, one or both of the insulating film 110 which is formed over the metal oxide 108 and the insulating film 104 which is formed below the metal oxide 108 contains excess oxygen. Oxygen or excess oxygen is transferred from one or both of the insulating film 104 and the insulating film 110 to the metal oxide 108, whereby oxygen vacancies in the metal oxide can be reduced.

Impurities such as hydrogen and moisture entering the metal oxide 108 adversely affect the transistor characteristics and therefore cause a problem. Thus, it is preferable that the amount of impurities such as hydrogen and moisture in the metal oxide 108 be as small as possible.

Note that it is preferable to use, as the metal oxide 108, a metal oxide in which the impurity concentration is low and the density of defect states is low, in which case the transistor having excellent electrical characteristics can be fabricated. Here, the state in which the impurity concentration is low and the density of defect states is low (the amount of oxygen vacancies is small) is referred to as highly purified intrinsic or substantially highly purified intrinsic. A highly purified intrinsic or substantially highly purified intrinsic metal oxide has few carrier generation sources, and thus can have a low carrier density. Thus, a transistor in which a channel region is formed in the metal oxide rarely has electrical characteristics with a negative threshold voltage (also referred to as normally-on). A highly purified intrinsic or substantially highly purified intrinsic metal oxide has a low density of defect states and accordingly has a low density of trap states in some cases. Furthermore, the highly purified intrinsic or substantially highly purified intrinsic metal oxide has an extremely low off-state current; thus, even an element having a channel width of 1×10⁶ μm and a channel length of 10 μm can have characteristics in which the off-state current is less than or equal to the measurement limit of a semiconductor parameter analyzer, that is, less than or equal to 1×10⁻¹³ A, at a voltage between a source electrode and a drain electrode (drain voltage) of 1 V to 10 V.

As illustrated in FIGS. 6(A), 6(B), and 6(C), the transistor 100 may further include an insulating film 118 over the insulating film 116, a conductive film 120 a electrically connected to the region 108 n through an opening 141 a formed in the insulating films 116 and 118; and a conductive film 120 b electrically connected to the region 108 n through an opening 141 b formed in the insulating films 116 and 118.

Note that in this specification and the like, the insulating film 104 may be referred to as a first insulating film, the insulating film 110 may be referred to as a second insulating film, the insulating film 116 may be referred to as a third insulating film, and the insulating film 118 may be referred to as a fourth insulating film. The conductive film 112, the conductive film 120 a, and the conductive film 120 b function as a gate electrode, a source electrode, and a drain electrode, respectively.

The insulating film 110 functions as a gate insulating film. The insulating film 110 includes an excess oxygen region. Since the insulating film 110 includes the excess oxygen region, excess oxygen can be supplied to the metal oxide 108. As a result, oxygen vacancies that might be formed in the metal oxide 108 can be filled with excess oxygen, and the semiconductor device having high reliability can be provided.

Note that to supply excess oxygen to the metal oxide 108, excess oxygen may be supplied to the insulating film 104 that is formed below the metal oxide 108. In that case, excess oxygen contained in the insulating film 104 might also be supplied to the regions 108 n. It is not desirable that excess oxygen be supplied to the regions 108 n because the resistance of the regions 108 n is increased. In contrast, in the structure in which the insulating film 110 formed over the metal oxide 108 contains excess oxygen, excess oxygen can be selectively supplied only to a region overlapping with the conductive film 112.

2-2. Components of Semiconductor Device

Next, components of the semiconductor device of this embodiment will be described in detail.

[Substrate]

Although there is no particular limitation on a material and the like of the substrate 102, the material needs to have heat resistance at least high enough to withstand heat treatment to be performed later. For example, a glass substrate, a ceramic substrate, a quartz substrate, a sapphire substrate, or the like may be used as the substrate 102. Alternatively, a single crystal semiconductor substrate or a polycrystalline semiconductor substrate made of silicon or silicon carbide, a compound semiconductor substrate made of silicon germanium or the like, an SOI substrate, or the like can be used, or any of these substrates provided with a semiconductor element may be used as the substrate 102. Note that in the case where a glass substrate is used as the substrate 102, a large-sized substrate having any of the following sizes is used: the 6th generation (1500 mm×1850 mm), the 7th generation (1870 mm×2200 mm), the 8th generation (2200 mm×2400 mm), the 9th generation (2400 mm×2800 mm), and the 10th generation (2950 mm×3400 mm); thus, a large-sized display device can be fabricated.

Alternatively, a flexible substrate may be used as the substrate 102, and the transistor 100 may be formed directly on the flexible substrate. Alternatively, a separation layer may be provided between the substrate 102 and the transistor 100. The separation layer can be used when part or the whole of a semiconductor device completed thereover is separated from the substrate 102 and transferred onto another substrate. In such a case, the transistor 100 can be transferred onto a substrate having low heat resistance or a flexible substrate as well.

[First Insulating Film]

The insulating film 104 can be formed by a sputtering method, a CVD method, an evaporation method, a pulsed laser deposition (PLD) method, a printing method, a coating method, or the like as appropriate. For example, the insulating film 104 can be formed to have a single layer or a stacked layer including an oxide insulating film or a nitride insulating film. To improve the properties of the interface with the metal oxide 108, at least a region of the insulating film 104 which is in contact with the metal oxide 108 is preferably formed using an oxide insulating film. When the insulating film 104 is formed using an oxide insulating film from which oxygen is released by heating, oxygen contained in the insulating film 104 can be moved to the metal oxide 108 by heat treatment.

The thickness of the insulating film 104 can be greater than or equal to 50 nm, greater than or equal to 100 nm and less than or equal to 3000 nm, or greater than or equal to 200 nm and less than or equal to 1000 nm. By increasing the thickness of the insulating film 104, the amount of oxygen released from the insulating film 104 can be increased; furthermore, interface states at the interface between the insulating film 104 and the metal oxide 108 and oxygen vacancies included in the metal oxide 108 can be reduced.

For example, the insulating film 104 can be formed to have a single layer or a stacked layer using silicon oxide, silicon oxynitride, silicon nitride oxide, silicon nitride, aluminum oxide, hafnium oxide, gallium oxide, a Ga—Zn oxide, or the like. In this embodiment, the insulating film 104 has a stacked-layer structure of a silicon nitride film and a silicon oxynitride film. With the insulating film 104 having such a stacked-layer structure using a silicon nitride film on a lower layer side and a silicon oxynitride film on an upper layer side, oxygen can be efficiently introduced into the metal oxide 108.

[Conductive Film]

The conductive film 112 functioning as a gate electrode, the conductive film 120 a functioning as a source electrode, and the conductive film 120 b functioning as a drain electrode can each be formed using a metal element selected from chromium (Cr), copper (Cu), aluminum (Al), gold (Au), silver (Ag), zinc (Zn), molybdenum (Mo), tantalum (Ta), titanium (Ti), tungsten (W), manganese (Mn), nickel (Ni), iron (Fe), and cobalt (Co); an alloy including these metal elements as its component; an alloy including a combination of these metal elements; or the like.

Furthermore, the conductive films 112, 120 a, and 120 b can be formed using an oxide conductor or a metal oxide, such as an oxide including indium and tin (In—Sn oxide), an oxide including indium and tungsten (In—W oxide), an oxide including indium, tungsten, and zinc (In—W—Zn oxide), an oxide including indium and titanium (In—Ti oxide), an oxide including indium, titanium, and tin (In—Ti—Sn oxide), an oxide including indium and zinc (In—Zn oxide), an oxide including indium, tin, and silicon (In—Sn—Si oxide), or an oxide including indium, gallium, and zinc (In—Ga—Zn oxide).

Here, an oxide conductor is described. In this specification and the like, an oxide conductor may be referred to as OC (Oxide Conductor). For example, oxygen vacancies are formed in a metal oxide, and then hydrogen is added to the oxygen vacancies, so that a donor level is formed in the vicinity of the conduction band. This increases the conductivity of the metal oxide; accordingly, the metal oxide becomes a conductor. The metal oxide having become a conductor can be referred to as an oxide conductor. Metal oxides generally have a visible light transmitting property because of their large energy gap. Meanwhile, an oxide conductor is a metal oxide having a donor level in the vicinity of the conduction band. Therefore, the influence of absorption due to the donor level is small in an oxide conductor, and an oxide conductor has a visible light transmitting property comparable to that of a metal oxide.

It is particularly preferred to use the oxide conductor described above for the conductive film 112, in which case excess oxygen can be added to the insulating film 110.

A Cu—X alloy film (X is Mn, Ni, Cr, Fe, Co, Mo, Ta, or Ti) may be used as the conductive films 112, 120 a, and 120 b. The use of a Cu—X alloy film enables fabrication costs to be reduced because processing can be performed by a wet etching process.

Among the above-mentioned metal elements, it is particularly preferable that any one or more selected from titanium, tungsten, tantalum, and molybdenum be included in the conductive films 112, 120 a, and 120 b. It is particularly preferable that a tantalum nitride film be used as each of the conductive films 112, 120 a, and 120 b. The tantalum nitride film has conductivity and a high barrier property against copper or hydrogen. Furthermore, since a tantalum nitride film releases little hydrogen from itself, it can be favorably used as the conductive film in contact with the metal oxide 108 or the conductive film in the vicinity of the metal oxide 108.

The conductive films 112, 120 a, and 120 b can be formed by electroless plating. As a material that can be deposited by electroless plating, for example, any one or more selected from Cu, Ni, Al, Au, Sn, Co, Ag, and Pd can be used. It is particularly favorable to use Cu or Ag because the resistance of the conductive film can be reduced.

[Second Insulating Film]

As the insulating film 110 functioning as a gate insulating film of the transistor 100, an insulating layer including one or more of the following films formed by a plasma enhanced chemical vapor deposition (PECVD) method, a sputtering method, or the like can be used: a silicon oxide film, a silicon oxynitride film, a silicon nitride oxide film, a silicon nitride film, an aluminum oxide film, a hafnium oxide film, an yttrium oxide film, a zirconium oxide film, a gallium oxide film, a tantalum oxide film, a magnesium oxide film, a lanthanum oxide film, a cerium oxide film, and a neodymium oxide film. Note that the insulating film 110 may have a stacked-layer structure of two layers or a stacked-layer structure of three or more layers.

The insulating film 110 that is in contact with the metal oxide 108 functioning as a channel region of the transistor 100 is preferably an oxide insulating film and preferably includes a region including oxygen in excess of that in the stoichiometric composition (excess oxygen region). In other words, the insulating film 110 is an insulating film capable of releasing oxygen. Note that in order to provide the excess oxygen region in the insulating film 110, the insulating film 110 is formed in an oxygen atmosphere, or the deposited insulating film 110 is subjected to heat treatment in an oxygen atmosphere, for example.

In the case of using hafnium oxide for the insulating film 110, the following effects are attained. Hafnium oxide has a higher dielectric constant than silicon oxide and silicon oxynitride. Therefore, the thickness of the insulating film 110 can be made large as compared with the case of using silicon oxide; thus, leakage current due to tunnel current can be low. That is, it is possible to achieve a transistor with a low off-state current. Moreover, hafnium oxide having a crystal structure has a higher dielectric constant than hafnium oxide having an amorphous structure. Therefore, it is preferable to use hafnium oxide having a crystal structure, in order to obtain a transistor with a low off-state current. Examples of the crystal structure include a monoclinic crystal structure and a cubic crystal structure. Note that one embodiment of the present invention is not limited to these.

It is preferable that the insulating film 110 have few defects and typically have as few signals observed by electron spin resonance (ESR) spectroscopy as possible. Examples of the signals include an E′ center observed at a g-factor of 2.001. Note that the E′ center is due to the dangling bond of silicon. As the insulating film 110, a silicon oxide film or a silicon oxynitride film whose spin density due to the E′ center is lower than or equal to 3×10¹⁷ spins/cm³ and preferably lower than or equal to 5×10¹⁶ spins/cm³ may be used.

[Metal Oxide]

As the metal oxide 108, the metal oxide described above can be used.

<Atomic Ratio>

Preferred ranges of the atomic ratio of indium, the element M, and zinc contained in the metal oxide according to the present invention are described below with reference to FIG. 16(A), FIG. 16(B), and FIG. 16(C). Note that the proportion of oxygen atoms is not illustrated in FIG. 16(A), FIG. 16(B), and FIG. 16(C). The terms of the atomic ratio of indium, the element M, and zinc contained in the metal oxide are denoted by [In], [M], and [Zn], respectively.

In FIG. 16(A), FIG. 16(B), and FIG. 16(C), dashed lines indicate a line where the atomic ratio of [In]:[M]:[Zn]=(1+α):(1−α):1 (−1≤α≤1), a line where the atomic ratio of [In]:[M]; [Zn]=(1+α):(1−α):2, a line where the atomic ratio of [In]:[M]:[Zn]=(1+α):(1−α):3, a line where the atomic ratio of [In]:[M]:[Zn]=(1+α):(1−α):4, and a line where the atomic ratio of [In]:[M]; [Zn]=(1+α):(1−α):5.

Dashed-dotted lines indicate a line representing the atomic ratio of [In]:[M]:[Zn]=5:1:β (β≥0), a line where the atomic ratio of [In]:[M]:[Zn]=2:1:β, a line where the atomic ratio of [In]:[M]:[Zn]=1:1:β, a line where the atomic ratio of [In]:[M]:[Zn]=1:2:β, a line where the atomic ratio of [In]:[M]:[Zn]=1:3:3, and a line where the atomic ratio of [In]:[M]:[Zn]=1:4:β.

A metal oxide having the atomic ratio of [In]:[M]:[Zn]=0:2:1 or a value in the neighborhood thereof in FIG. 16(A), FIG. 16(B), and FIG. 16(C) tends to have a spinel crystal structure.

A plurality of phases coexist in the metal oxide in some cases (two-phase coexistence, three-phase coexistence, or the like). For example, in the case where the atomic ratio is in the neighborhood of [In]:[M]:[Zn]=0:2:1, two phases of a spinel crystal structure and a layered crystal structure are likely to coexist. In addition, in the case where the atomic ratio is in the neighborhood of [In]:[M]:[Zn]=1:0:0, two phases of a bixbyite crystal structure and a layered crystal structure are likely to coexist. In the case where a plurality of phases coexist in the metal oxide, a grain boundary might be formed between different crystal structures.

A region A in FIG. 16(A) shows an example of the preferred ranges of the atomic ratio of indium to the element M and zinc contained in a metal oxide.

When the indium content of the metal oxide is increased, the carrier mobility (electron mobility) of the metal oxide can be increased. Thus, a metal oxide having a high content of indium has higher carrier mobility than a metal oxide having a low content of indium.

In contrast, when the indium content and the zinc content of a metal oxide become lower, carrier mobility becomes lower. Thus, in the case of an atomic ratio of [In]:[M]:[Zn]=0:1:0 and a value in the neighborhood thereof (e.g., a region C in FIG. 16(C)), insulation performance becomes better.

Accordingly, the metal oxide of one embodiment of the present invention preferably has an atomic ratio represented by the region A in FIG. 16(A), with which high carrier mobility is obtained.

In the region A, particularly in a region B in FIG. 16(B), an excellent metal oxide having high carrier mobility and high reliability can be obtained.

Note that the region B has an atomic ratio of [In]:[M]:[Zn]=4:2:3 to 4.1 and values in the neighborhood thereof. The neighborhood includes an atomic ratio of [In]:[M]:[Zn]=5:3:4, for example. Note that the region B has an atomic ratio of [In]:[M]:[Zn]=5:1:6 and values in the neighborhood thereof, and an atomic ratio of [In]:[M]:[Zn]=5:1:7 and values in the neighborhood thereof.

Note that the property of a metal oxide is not uniquely determined by an atomic ratio. Even with the same atomic ratio, the property of a metal oxide might be different depending on a formation condition. For example, in the case where the metal oxide film is formed with a sputtering apparatus, a film having an atomic ratio deviated from the atomic ratio of a target is formed. Furthermore, [Zn] in the film might be smaller than [Zn] in the target depending on the substrate temperature in film formation. Thus, the illustrated regions are each a region representing an atomic ratio with which a metal oxide tends to have specific characteristics, and boundaries of the region A to the region C are not clear.

In the case where the metal oxide 108 is an In-M-Zn oxide, it is preferable to use a target including polycrystalline In-M-Zn oxide as the sputtering target. Note that the atomic ratio of the formed metal oxide 108 varies from the above atomic ratios of metal elements included in the sputtering targets in a range of ±40%. For example, when a sputtering target used for the metal oxide 108 has a composition of In:Ga:Zn=4:2:4.1 [atomic ratio], the composition of the formed metal oxide 108 may be In:Ga:Zn=4:2:3 [atomic ratio] or in the neighborhood thereof. When a sputtering target used for the metal oxide 108 has a composition of In:Ga:Zn=5:1:7 [atomic ratio], the composition of the formed metal oxide 108 may be 5:1:6 [atomic ratio] or in the neighborhood thereof.

The energy gap of the metal oxide 108 is 2 eV or more, preferably 2.5 eV or more. With the use of a metal oxide having such a wide energy gap, the off-state current of the transistor 100 can be reduced.

Furthermore, the metal oxide 108 preferably has a non-single-crystal structure. Examples of the non-single-crystal structure include a CAAC-OS which will be described later, a polycrystalline structure, a microcrystalline structure, and an amorphous structure. Among the non-single-crystal structures, an amorphous structure has the highest density of defect states.

[Third Insulating Film]

The insulating film 116 contains nitrogen or hydrogen. A nitride insulating film can be given as the insulating film 116, for example. The nitride insulating film can be formed using silicon nitride, silicon nitride oxide, silicon oxynitride, or the like. The hydrogen concentration in the insulating film 116 is preferably higher than or equal to 1×10²² atoms/cm³. The insulating film 116 is in contact with the regions 108 n of the metal oxide 108. Thus, the concentration of an impurity (e.g., hydrogen) in the regions 108 n in contact with the insulating film 116 is increased, leading to an increase in the carrier density of the regions 108 n.

[Fourth Insulating Film]

As the insulating film 118, an oxide insulating film can be used. Alternatively, a layered film of an oxide insulating film and a nitride insulating film can be used as the insulating film 118. The insulating film 118 can be formed using, for example, silicon oxide, silicon oxynitride, silicon nitride oxide, aluminum oxide, hafnium oxide, gallium oxide, Ga—Zn oxide, or the like.

Furthermore, the insulating film 118 is preferably a film functioning as a barrier film against hydrogen, water, and the like from the outside.

The thickness of the insulating film 118 can be greater than or equal to 30 nm and less than or equal to 500 nm, or greater than or equal to 100 nm and less than or equal to 400 nm.

2-3. Structure Example 2 of Transistor

Next, a structure of a transistor different from that in FIGS. 6(A), 6(B), and 6(C) will be described with reference to FIGS. 7(A), 7(B), and 7(C)

FIG. 7(A) is a top view of the transistor 150; FIG. 7(B) is a cross-sectional view taken along dashed-dotted line X1-X2 in FIG. 7(A); and FIG. 7(C) is a cross-sectional view taken along dashed-dotted line Y1-Y2 in FIG. 7(A).

The transistor 150 illustrated in FIGS. 7(A), 7(B), and 7(C) includes the conductive film 106 over the substrate 102; the insulating film 104 over the conductive film 106; the metal oxide 108 over the insulating film 104; the insulating film 110 over the metal oxide 108; the conductive film 112 over the insulating film 110; and the insulating film 116 over the insulating film 104, the metal oxide 108, and the conductive film 112.

Note that the metal oxide 108 has a structure similar to that in the transistor 100 shown in FIGS. 6(A), 6(B), and 6(C). The transistor 150 shown in FIGS. 7(A), 7(B), and 7(C) includes the conductive film 106 and an opening 143 in addition to the components of the transistor 100 described above.

The opening 143 is provided in the insulating films 104 and 110. The conductive film 106 is electrically connected to the conductive film 112 through the opening 143. Thus, the same potential is applied to the conductive film 106 and the conductive film 112. Note that different potentials may be applied to the conductive film 106 and the conductive film 112 without providing the opening 143. Alternatively, the conductive film 106 may be used as a light-blocking film without providing the opening 143. When the conductive film 106 is formed using a light-blocking material, for example, light from the bottom with which the metal oxide 108 is irradiated can be reduced.

In the case of the structure of the transistor 150, the conductive film 106 functions as a first gate electrode (also referred to as a bottom-gate electrode), and the conductive film 112 functions as a second gate electrode (also referred to as a top-gate electrode). The insulating film 104 functions as a first gate insulating film, and the insulating film 110 functions as a second gate insulating film.

The conductive film 106 can be formed using a material similar to the above-described materials of the conductive films 112, 120 a, and 120 b. It is particularly suitable to use a material containing copper for formation of the conductive film 106 because the resistance can be reduced. It is favorable that, for example, the conductive film 106 have a stacked-layer structure in which a copper film is provided over a titanium nitride film, a tantalum nitride film, or a tungsten film, and that the conductive films 120 a and 120 b have a stacked-layer structure in which a copper film is provided over a titanium nitride film, a tantalum nitride film, or a tungsten film. In that case, by using the transistor 150 as one or both of a pixel transistor and a driving transistor of a display device, parasitic capacitance generated between the conductive film 106 and the conductive film 120 a and parasitic capacitance generated between the conductive film 106 and the conductive film 120 b can be reduced. Thus, the conductive film 106, the conductive film 120 a, and the conductive film 120 b can be used not only as the first gate electrode, the source electrode, and the drain electrode of the transistor 150, but also as power supply wirings, signal supply wirings, connection wirings, or the like of the display device.

In this manner, unlike the transistor 100 described above, the transistor 150 in FIGS. 7(A), 7(B), and 7(C) has a structure including a conductive film functioning as a gate electrode over and under the metal oxide 108. As in the transistor 150, a semiconductor device of one embodiment of the present invention may be provided with a plurality of gate electrodes.

As illustrated in FIGS. 7(B) and 7(C), the metal oxide 108 is positioned to face each of the conductive film 106 functioning as a first gate electrode and the conductive film 112 functioning as a second gate electrode and is sandwiched between the two conductive films functioning as the gate electrodes.

Furthermore, the length of the conductive film 112 in the channel width direction is larger than the length of the metal oxide 108 in the channel width direction. In the channel width direction, the whole metal oxide 108 is covered with the conductive film 112 with the insulating film 110 placed therebetween. Since the conductive film 112 is connected to the conductive film 106 through the opening 143 provided in the insulating film 104 and the insulating film 110, one of side surfaces of the metal oxide 108 in the channel width direction faces the conductive film 112 with the insulating film 110 placed therebetween.

In other words, the conductive film 106 and the conductive film 112 are connected through the opening 143 provided in the insulating films 104 and 110, and each include a region positioned outside a side edge portion of the metal oxide 108.

Such a structure enables the metal oxide 108 included in the transistor 150 to be electrically surrounded by electric fields of the conductive film 106 functioning as a first gate electrode and the conductive film 112 functioning as a second gate electrode. A device structure of a transistor, like that of the transistor 150, in which electric fields of the first gate electrode and the second gate electrode electrically surround the metal oxide 108 where a channel region is formed can be referred to as a Surrounded channel (S-channel) structure.

Since the transistor 150 has the S-channel structure, an electric field for inducing a channel can be effectively applied to the metal oxide 108 by the conductive film 106 or the conductive film 112; thus, the current drive capability of the transistor 150 can be improved and high on-state current characteristics can be obtained. Since the on-state current can be increased, it is possible to reduce the size of the transistor 150. Furthermore, since the transistor 150 has a structure in which the metal oxide 108 is surrounded by the conductive film 106 and the conductive film 112, the mechanical strength of the transistor 150 can be increased.

Note that in the channel width direction of the transistor 150, an opening different from the opening 143 may be formed on the side of the metal oxide 108 on which the opening 143 is not formed.

When a transistor has a pair of gate electrodes between which a semiconductor film is positioned as in the transistor 150, one of the gate electrodes may be supplied with a signal A, and the other gate electrode may be supplied with a fixed potential V_(b). Alternatively, one of the gate electrodes may be supplied with the signal A, and the other gate electrode may be supplied with a signal B. Alternatively, one of the gate electrodes may be supplied with a fixed potential V_(a), and the other gate electrode may be supplied with the fixed potential V_(b).

The signal A is, for example, a signal for controlling the on state or the off state. The signal A may be a digital signal with two kinds of potentials, a potential V1 and a potential V2 (V1>V2). For example, the potential V1 can be a high power supply potential, and the potential V2 can be a low power supply potential. The signal A may be an analog signal.

The fixed potential V_(b) is, for example, a potential for controlling a threshold voltage V_(thA) of the transistor. The fixed potential V_(b) may be the potential V1 or the potential V2. In that case, a potential generator circuit for generating the fixed potential V_(b) is not necessarily provided separately, which is preferable. The fixed potential V_(b) may be a potential different from the potential V1 or the potential V2. When the fixed potential V_(b) is low, the threshold voltage V_(thA) can be high in some cases. As a result, the drain current when the gate-source voltage V_(g)s is 0 V can be reduced, and leakage current in a circuit including the transistor can be reduced in some cases. The fixed potential V_(b) may be, for example, lower than the low power supply potential. Meanwhile, a high fixed potential V_(b) can lower the threshold voltage V_(thA) in some cases. As a result, the drain current when the gate-source voltage V_(g)s is a high power supply potential can be increased and the operating speed of the circuit including the transistor can be increased in some cases. The fixed potential V_(b) may be, for example, higher than the low power supply potential.

The signal B is, for example, a signal for controlling the on state or the off state. The signal B may be a digital signal with two kinds of potentials, a potential V3 and a potential V4 (V3>V4). For example, the potential V3 can be a high power supply potential, and the potential V4 can be a low power supply potential. The signal B may be an analog signal.

When both the signal A and the signal B are digital signals, the signal B may be a signal having the same digital value as the signal A. In this case, it may be possible to increase the on-state current of the transistor and increase the operating speed of the circuit including the transistor. Here, the potential V1 and the potential V2 of the signal A may be different from the potential V3 and the potential V4 of the signal B. For example, if a gate insulating film for the gate to which the signal B is input is thicker than a gate insulating film for the gate to which the signal A is input, the potential amplitude of the signal B (V3−V4) may be larger than the potential amplitude of the signal A (V1−V2). In this manner, the influence of the signal A and the influence of the signal B on the on state or the off state of the transistor can be substantially the same in some cases.

When both the signal A and the signal B are digital signals, the signal B may be a signal having a digital value different from that of the signal A. In this case, the signal A and the signal B can separately control the transistor, and thus, higher performance can be achieved in some cases. The transistor which is, for example, an n-channel transistor can function by itself as a NAND circuit, a NOR circuit, or the like in the following case: the transistor is turned on only when the signal A has the potential V1 and the signal B has the potential V3, or the transistor is turned off only when the signal A has the potential V2 and the signal B has the potential V4. The signal B may be a signal for controlling the threshold voltage V_(thA). The signal B may be a signal whose potential is different between a period in which the circuit including the transistor operates and a period in which the circuit does not operate. The signal B may be a signal whose potential varies depending on the operation mode of the circuit. In this case, the potential of the signal B is not changed as frequently as the potential of the signal A in some cases.

When both the signal A and the signal B are analog signals, the signal B may be an analog signal having the same potential as the signal A, an analog signal whose potential is a constant times the potential of the signal A, an analog signal whose potential is higher or lower than the potential of the signal A by a constant, or the like. In this case, it may be possible to increase the on-state current of the transistor and increase the operating speed of the circuit including the transistor. The signal B may be an analog signal different from the signal A. In this case, the signal A and the signal B can separately control the transistor, and thus, higher performance can be achieved in some cases.

The signal A may be a digital signal, and the signal B may be an analog signal. Alternatively, the signal A may be an analog signal, and the signal B may be a digital signal.

When both of the gate electrodes of the transistor are supplied with the fixed potentials, the transistor can function as an element equivalent to a resistor in some cases. For example, in the case where the transistor is of an n-channel type, the effective resistance of the transistor can be sometimes low (high) when the fixed potential V_(a) or the fixed potential V_(b) is high (low). When both the fixed potential V_(a) and the fixed potential V_(b) are high (low), the effective resistance lower (higher) than the effective resistance of a transistor with only one gate can be obtained in some cases.

Note that the other components of the transistor 150 are similar to those of the transistor 100 described above and have similar effects.

An insulating film may further be formed over the transistor 150. The transistor 150 illustrated in FIGS. 7(A), 7(B), and 7(C) includes an insulating film 122 over the conductive films 120 a and 120 b and the insulating film 118.

The insulating film 122 has a function of covering unevenness and the like caused by the transistor or the like. The insulating film 122 has an insulating property and is formed using an inorganic material or an organic material. Examples of the inorganic material include a silicon oxide film, a silicon oxynitride film, a silicon nitride oxide film, a silicon nitride film, an aluminum oxide film, and an aluminum nitride film. Examples of the organic material include photosensitive resin materials such as an acrylic resin and a polyimide resin.

2-4. Structure Example 3 of Transistor

Next, a structure different from that of the transistor 150 in FIGS. 7(A), 7(B), and 7(C) will be described with reference to FIG. 8 .

FIGS. 8(A) and 8(B) are cross-sectional views of a transistor 160. Note that the top view of the transistor 160 is similar to that of the transistor 150 in FIG. 7(A), and therefore the description is omitted here.

The transistor 160 illustrated in FIGS. 8(A) and 8(B) is different from the transistor 150 in the stacked-layer structure of the conductive film 112, the shape of the conductive film 112, and the shape of the insulating film 110.

The conductive film 112 in the transistor 160 includes a conductive film 112_1 over the insulating film 110 and a conductive film 112_2 over the conductive film 112_1. For example, an oxide conductive film is used as the conductive film 112_1, so that excess oxygen can be added to the insulating film 110. The oxide conductive film is formed by a sputtering method in an atmosphere containing an oxygen gas. As the oxide conductive film, an oxide including indium and tin, an oxide including tungsten and indium, an oxide including tungsten, indium, and zinc, an oxide including titanium and indium, an oxide including titanium, indium, and tin, an oxide including indium and zinc, an oxide including silicon, indium, and tin, an oxide including indium, gallium, and zinc, or the like can be used, for example.

As illustrated in FIG. 8(B), the conductive film 112_2 is connected to the conductive film 106 through the opening 143. When the opening 143 is formed, the opening 143 is formed after a conductive film to be the conductive film 112_1 is formed, so that the shape illustrated in FIG. 8(B) can be obtained. In the case where an oxide conductive film is used as the conductive film 112_1, the structure in which the conductive film 112_2 is connected to the conductive film 106 can reduces the contact resistance between the conductive film 112 and the conductive film 106.

The conductive film 112 and the insulating film 110 in the transistor 160 have a tapered shape. More specifically, the lower edge portion of the conductive film 112 is formed outside the upper edge portion of the conductive film 112. The lower edge portion of the insulating film 110 is formed outside the upper edge portion of the insulating film 110. In addition, the lower edge portion of the conductive film 112 is formed in substantially the same position as that of the upper edge portion of the insulating film 110.

The transistor 160 in which the conductive film 112 and the insulating film 110 have a tapered shape is suitable because coverage with the insulating film 116 can be increased as compared with the transistor 160 in which the conductive film 112 and the insulating film 110 have a rectangular shape.

Note that the other components of the transistor 160 are similar to those of the transistor 150 described above and have similar effects.

2-5. Method for Manufacturing Semiconductor Device

Next, an example of a method for manufacturing the transistor 150 illustrated in FIGS. 7(A), 7(B), and 7(C) will be described with reference to FIG. 9 to FIG. 11 . Note that FIG. 9 to FIG. 11 are cross-sectional views in the channel length direction and the channel width direction illustrating the method for manufacturing the transistor 150.

First, the conductive film 106 is formed over the substrate 102. Next, the insulating film 104 is formed over the substrate 102 and the conductive film 106, and a metal oxide film is formed over the insulating film 104. Then, the metal oxide film is processed into an island shape, whereby a metal oxide 108 a is formed (see FIG. 9(A)).

The conductive film 106 can be formed by selecting the above-mentioned materials. In this embodiment, as the conductive film 106, a stacked film of a 50-nm-thick tungsten film and a 400-nm-thick copper film is formed with a sputtering apparatus.

Note that as a method for processing a conductive film to be the conductive film 106, one or both of a wet etching method and a dry etching method can be used. In this embodiment, the conductive film is processed by etching the copper film by a wet etching method and then etching the tungsten film by a dry etching method to form the conductive film 106.

The insulating film 104 can be formed by a sputtering method, a CVD method, an evaporation method, a pulsed laser deposition (PLD) method, a printing method, a coating method, or the like as appropriate. In this embodiment, as the insulating film 104, a 400-nm-thick silicon nitride film and a 50-nm-thick silicon oxynitride film are formed with a PECVD apparatus.

After the insulating film 104 is formed, oxygen may be added to the insulating film 104. As oxygen added to the insulating film 104, an oxygen radical, an oxygen atom, an oxygen atomic ion, an oxygen molecular ion, or the like may be used. As an addition method, an ion doping method, an ion implantation method, a plasma treatment method, or the like is given. Alternatively, a film that suppresses oxygen release may be formed over the insulating film 104, and then oxygen may be added to the insulating film 104 through the film.

The film that suppresses oxygen release can be formed using a conductive film or a semiconductor film containing one or more of indium, zinc, gallium, tin, aluminum, chromium, tantalum, titanium, molybdenum, nickel, iron, cobalt, and tungsten.

In the case where oxygen is added by plasma treatment, oxygen is excited by a microwave to generate high-density oxygen plasma, whereby the amount of oxygen added to the insulating film 104 can be increased.

In forming the metal oxide 108 a, an inert gas (e.g., a helium gas, an argon gas, or a xenon gas) may be mixed in addition to the oxygen gas. Note that the proportion of the oxygen gas in the whole deposition gas (hereinafter also referred to as an oxygen flow rate ratio) in forming the metal oxide 108 a is higher than or equal to 0% and lower than or equal to 30%, preferably higher than or equal to 5% and lower than or equal to 20%.

Conditions for forming the metal oxide 108 a are as follows: the substrate temperature is higher than or equal to room temperature and lower than or equal to 180° C., and the substrate temperature is preferably higher than or equal to room temperature and lower than or equal to 140° C. The substrate temperature at the time of forming the metal oxide 108 a is preferably, for example, higher than or equal to room temperature and lower than 140° C. because the productivity is increased.

The thickness of the metal oxide 108 a is greater than or equal to 3 nm and less than or equal to 200 nm, preferably greater than or equal to 3 nm and less than or equal to 100 nm, further preferably greater than or equal to 3 nm and less than or equal to 60 nm.

Note that in the case where a large-sized glass substrate (e.g., the 6th generation to the 10th generation) is used as the substrate 102 and in the case where the substrate temperature in forming the metal oxide 108 a is higher than or equal to 200° C. and lower than or equal to 300° C., the substrate 102 might be changed in shape (distorted or warped). Therefore, in the case where a large-sized glass substrate is used, the change in the shape of the glass substrate can be suppressed by setting the substrate temperature in forming the metal oxide 108 a to higher than or equal to room temperature and lower than 200° C.

In addition, increasing the purity of the sputtering gas is necessary. For example, as an oxygen gas or an argon gas used for a sputtering gas, a gas highly purified to have a dew point of −40° C. or lower, preferably −80° C. or lower, further preferably −100° C. or lower, still further preferably −120° C. or lower is used, whereby entry of moisture or the like into the metal oxide can be prevented as much as possible.

In the case where the metal oxide film is formed by a sputtering method, a chamber in a sputtering apparatus is preferably evacuated to be a high vacuum (to the degree of about 5×10⁻⁷ Pa to 1×10⁻⁴ Pa) with an adsorption vacuum evacuation pump such as a cryopump in order to remove water or the like, which serves as an impurity for the metal oxide, as much as possible. In particular, the partial pressure of gas molecules corresponding to H₂O (gas molecules corresponding to m/z=18) in the chamber in the standby mode of the sputtering apparatus is preferably lower than or equal to 1×10⁻⁴ Pa, further preferably lower than or equal to 5×10⁻⁵ Pa.

In this embodiment, the formation conditions of the metal oxide 108 a are as follows.

The metal oxide 108 a is formed under the following formation conditions: an In—Ga—Zn metal oxide target is used and a sputtering method is used. The substrate temperature and the oxygen flow rate ratio at the time of film formation of the metal oxide 108 a can be set as appropriate. The pressure in a chamber is 0.6 Pa, and an AC power of 2500 W is supplied to the metal oxide target provided in the sputtering apparatus, whereby the oxide is formed.

Note that to process the formed metal oxide film into the metal oxide 108 a, one or both of a wet etching method and a dry etching method can be used.

After the metal oxide 108 a is formed, heat treatment may be performed to dehydrate or dehydrogenate the metal oxide 108 a. The temperature of the heat treatment is typically higher than or equal to 150° C. and lower than the strain point of the substrate, higher than or equal to 250° C. and lower than or equal to 450° C., or higher than or equal to 300° C. and lower than or equal to 450° C.

The heat treatment can be performed in an inert atmosphere containing nitrogen or a rare gas such as helium, neon, argon, xenon, or krypton. Alternatively, heating may be performed in an inert atmosphere, and then heating may be performed in an oxygen atmosphere. Note that it is preferable that the above inert atmosphere and oxygen atmosphere not contain hydrogen, water, or the like. The treatment time may be longer than or equal to 3 minutes and shorter than or equal to 24 hours.

An electric furnace, an RTA apparatus, or the like can be used for the heat treatment. With the use of an RTA apparatus, the heat treatment can be performed at a temperature higher than or equal to the strain point of the substrate only for a short time. Therefore, the heat treatment time can be shortened.

When the metal oxide film is formed while being heated or heat treatment is performed after the metal oxide is formed, the hydrogen concentration in the metal oxide, which is measured by SIMS, can be 5×10¹⁹ atoms/cm³ or lower, 1×10¹⁹ atoms/cm³ or lower, 5×10¹⁸ atoms/cm³ or lower, 1×10¹⁸ atoms/cm³ or lower, 5×10¹⁷ atoms/cm³ or lower, or 1×10¹⁶ atoms/cm³ or lower.

Next, an insulating film 110_0 is formed over the insulating film 104 and the metal oxide 108 a (see FIG. 9(B)).

As the insulating film 110_0, a silicon oxide film or a silicon oxynitride film can be formed with a plasma-enhanced chemical vapor deposition apparatus (also referred to as a PECVD apparatus or simply a plasma CVD apparatus). In this case, a deposition gas containing silicon and an oxidizing gas are preferably used as a source gas. Typical examples of the deposition gas containing silicon include silane, disilane, trisilane, and silane fluoride. Examples of the oxidizing gas include oxygen, ozone, dinitrogen monoxide, and nitrogen dioxide.

A silicon oxynitride film having a small amount of defects can be formed as the insulating film 110_0 with the PECVD apparatus in which the flow rate of the oxidizing gas is more than 20 times and less than 100 times, or more than or equal to 40 times and less than or equal to 80 times the flow rate of the deposition gas and the pressure in a treatment chamber is lower than 100 Pa or lower than or equal to 50 Pa.

As the insulating film 110_0, a dense silicon oxide film or a dense silicon oxynitride film can be formed under the following conditions: the substrate placed in a vacuum-evacuated treatment chamber of the PECVD apparatus is held at a temperature higher than or equal to 280° C. and lower than or equal to 400° C.; the pressure in the treatment chamber into which a source gas is introduced is set to be higher than or equal to 20 Pa and lower than or equal to 250 Pa, preferably higher than or equal to 100 Pa and lower than or equal to 250 Pa; and a high-frequency power is supplied to an electrode provided in the treatment chamber.

The insulating film 110_0 may be formed by a PECVD method using a microwave. A microwave refers to a wave in the frequency range of 300 MHz to 300 GHz. In the case of using a microwave, electron temperature and electron energy are low. Furthermore, in supplied power, the proportion of power used for acceleration of electrons is low, and power can be used for dissociation and ionization of more molecules; thus, plasma with a high density (high-density plasma) can be excited. Accordingly, with little plasma damage to the deposition surface or a deposit, the insulating film 110_0 having few defects can be formed.

Alternatively, the insulating film 110_0 can be formed by a CVD method using an organosilane gas. As the organosilane gas, any of the following silicon-containing compounds can be used: tetraethyl orthosilicate (TEOS: chemical formula Si(OC₂H₅)₄); tetramethylsilane (TMS: chemical formula Si(CH₃)₄); tetramethylcyclotetrasiloxane (TMCTS); octamethylcyclotetrasiloxane (OMCTS); hexamethyldisilazane (HMDS); triethoxysilane (SiH(OC₂H₅)₃); trisdimethylaminosilane (SiH(N(CH₃)₂)₃); and the like. The insulating film 110_0 having high coverage can be formed by a CVD method using an organosilane gas.

In this embodiment, as the insulating film 110_0, a 100-nm-thick silicon oxynitride film is formed with the PECVD apparatus.

Subsequently, a mask is formed by lithography in a desired position over the insulating film 110_0, and then the insulating film 110_0 and the insulating film 104 are partly etched, so that the opening 143 reaching the conductive film 106 is formed (see FIG. 9(C)).

To form the opening 143, one or both of a wet etching method and a dry etching method can be used. In this embodiment, the opening 143 is formed by a dry etching method.

Next, a conductive film 112_0 is formed over the conductive film 106 and the insulating film 110_0 so as to cover the opening 143. In the case where a metal oxide film is used as the conductive film 112_0, for example, oxygen might be added to the insulating film 110_0 during the formation of the conductive film 112_0 (see FIG. 9(D)).

Note that in FIG. 9(D), oxygen added to the insulating film 110_0 is schematically shown by arrows. Furthermore, the conductive film 112_0 formed to cover the opening 143 is electrically connected to the conductive film 106.

In the case where a metal oxide film is used as the conductive film 112_0, the conductive film 112_0 is preferably formed by a sputtering method in an atmosphere containing an oxygen gas. Formation of the conductive film 112_0 in an atmosphere containing an oxygen gas allows suitable addition of oxygen to the insulating film 110_0. Note that a method for forming the conductive film 112_0 is not limited to a sputtering method, and another method such as an ALD method may be used.

In this embodiment, a 100-nm-thick IGZO film containing an In—Ga—Zn oxide (In:Ga:Zn=4:2:4.1 (atomic ratio)) is formed as the conductive film 112_0 by a sputtering method. Oxygen addition treatment may be performed on the insulating film 110_0 before or after the formation of the conductive film 112_0. The oxygen addition treatment can be performed in a manner similar to that of the oxygen addition treatment that can be performed after the formation of the insulating film 104.

Subsequently, a mask 140 is formed by a lithography process in a desired position over the conductive film 112_0 (see FIG. 10(A)).

Next, etching is performed from above the mask 140 to process the conductive film 112_0 and the insulating film 110_0. After the processing of the conductive film 112_0 and the insulating film 110_0, the mask 140 is removed. As a result of the processing of the conductive film 112_0 and the insulating film 110_0, the island-shaped conductive film 112 and the island-shaped insulating film 110 are formed (see FIG. 10(B)).

In this embodiment, the conductive film 112_0 and the insulating film 110_0 are processed by a dry etching method.

In the processing of the conductive film 112_0 and the insulating film 110_0, the thickness of the metal oxide 108 a in a region not overlapping with the conductive film 112 is reduced in some cases. In other cases, in the processing of the conductive film 112_0 and the insulating film 110_0, the thickness of the insulating film 104 in a region not overlapping with the metal oxide 108 a is reduced. In the processing of the conductive film 112_0 and the insulating film 110_0, an etchant or an etching gas (e.g., chlorine) might be added to the metal oxide 108 a or the constituent element of the conductive film 112_0 or the insulating film 110_0 might be added to the metal oxide 108.

Next, the insulating film 116 is formed over the insulating film 104, the metal oxide 108, and the conductive film 112. By the formation of the insulating film 116, part of the metal oxide 108 a that is in contact with the insulating film 116 becomes the regions 108 n. Here, the metal oxide 108 a overlapping with the conductive film 112 is the metal oxide 108 (see FIG. 10(C)).

The insulating film 116 can be formed using a material selected from the above-mentioned materials. In this embodiment, as the insulating film 116, a 100-nm-thick silicon nitride oxide film is formed with a PECVD apparatus. In the formation of the silicon nitride oxide film, two steps, i.e., plasma treatment and deposition treatment, are performed at a temperature of 220° C. The plasma treatment is performed under the following conditions: an argon gas at a flow rate of 100 sccm and a nitrogen gas at a flow rate of 1000 sccm are introduced into a chamber before deposition; the pressure in the chamber is set to 40 Pa; and a power of 1000 W is supplied to an RF power source (27.12 MHz). The deposition treatment is performed under the following conditions: a silane gas at a flow rate of 50 sccm, a nitrogen gas at a flow rate of 5000 sccm, and an ammonia gas at a flow rate of 100 sccm are introduced into the chamber; the pressure in the chamber is set to 100 Pa; and a power of 1000 W is supplied to the RF power source (27.12 MHz).

When a silicon nitride oxide film is used as the insulating film 116, nitrogen or hydrogen in the silicon nitride oxide film can be supplied to the regions 108 n in contact with the insulating film 116. In addition, when the formation temperature of the insulating film 116 is the above temperature, release of excess oxygen contained in the insulating film 110 to the outside can be suppressed.

Next, the insulating film 118 is formed over the insulating film 116 (see FIG. 11(A)).

The insulating film 118 can be formed using a material selected from the above-mentioned materials. In this embodiment, as the insulating film 118, a 300-nm-thick silicon oxynitride film is formed with a PECVD apparatus.

Subsequently, a mask is formed by lithography in a desired position over the insulating film 118, and then the insulating film 118 and the insulating film 116 are partly etched, so that the opening 141 a and the opening 141 b reaching the regions 108 n are formed (see FIG. 11(B)).

To etch the insulating film 118 and the insulating film 116, one or both of a wet etching method and a dry etching method can be used. In this embodiment, the insulating film 118 and the insulating film 116 are processed by a dry etching method.

Next, a conductive film is formed over the regions 108 n and the insulating film 118 so as to cover the openings 141 a and 141 b, and the conductive film is processed into a desired shape, whereby the conductive films 120 a and 120 b are formed (see FIG. 11(C)).

The conductive films 120 a and 120 b can be formed by selecting the above-mentioned materials. In this embodiment, as the conductive films 120 a and 120 b, a stacked film of a 50-nm-thick tungsten film and a 400-nm-thick copper film is formed with a sputtering apparatus.

Note that as a method for processing a conductive film to be the conductive films 120 a and 120 b, one or both of a wet etching method and a dry etching method can be used. In this embodiment, the conductive film is processed by etching the copper film by a wet etching method and then etching the tungsten film by a dry etching method to form the conductive films 120 a and 120 b.

Then, the insulating film 122 is formed to cover the conductive films 120 a and 120 b and the insulating film 118.

Through the above steps, the transistor 150 shown in FIGS. 7(A), 7(B), and 7(C) can be manufactured.

Note that the films included in the transistor 150 (the insulating film, the metal oxide film, the conductive film, and the like) can be formed by, other than the above methods, a sputtering method, a chemical vapor deposition (CVD) method, a vacuum evaporation method, a pulsed laser deposition (PLD) method, or an ALD method. Alternatively, a coating method or a printing method can be used. Although a sputtering method and a plasma-enhanced chemical vapor deposition (PECVD) method are typical examples of the deposition method, a thermal CVD method may be used. As an example of a thermal CVD method, a metal organic chemical vapor deposition (MOCVD) method can be given.

Deposition by the thermal CVD method may be performed in such a manner that the pressure in a chamber is set to an atmospheric pressure or a reduced pressure, and a source gas and an oxidizer are supplied to the chamber at a time and react with each other in the vicinity of the substrate or over the substrate. Thus, no plasma is generated in the deposition; therefore, the thermal CVD method has an advantage that no defect due to plasma damage is caused.

The films such as the conductive films, the insulating films, and the metal oxide films that are described above can be formed by a thermal CVD method such as an MOCVD method.

For example, in the case where a hafnium oxide film is formed with a deposition apparatus employing an ALD method, two kinds of gases are used, namely, ozone (O₃) as an oxidizer and a source gas that is obtained by vaporizing liquid containing a solvent and a hafnium precursor (hafnium alkoxide or hafnium amide such as tetrakis(dimethylamide)hafnium (TDMAH, Hf[N(CH₃)₂]₄) or tetrakis(ethylmethylamide)hafnium).

In the case where an aluminum oxide film is formed with a deposition apparatus employing an ALD method, two kinds of gases are used, namely, H₂O as an oxidizer and a source gas that is obtained by vaporizing liquid containing a solvent and an aluminum precursor (e.g., trimethylaluminum (TMA, Al(CH₃)₃)). Examples of another material include tris(dimethylamide)aluminum, triisobutylaluminum, and aluminum tris(2,2,6,6-tetramethyl-3,5-heptanedionate).

In the case where a silicon oxide film is formed with a deposition apparatus employing an ALD method, hexachlorodisilane is adsorbed on a surface on which a film is to be formed, and radicals of an oxidizing gas (O₂ or dinitrogen monoxide) are supplied to react with the adsorbate.

In the case where a tungsten film is formed with a deposition apparatus employing an ALD method, a WF₆ gas and a B₂H₆ gas are sequentially introduced to form an initial tungsten film, and then, a WF₆ gas and an H₂ gas are used to form a tungsten film. Note that an SiH₄ gas may be used instead of a B₂H₆ gas.

In the case where a metal oxide such as an In—Ga—Zn—O film is formed with a deposition apparatus employing an ALD method, an In(CH₃)₃ gas and an O₃ gas) are used to form an In—O layer, a Ga(CH₃)₃ gas and an O₃ gas) are used to form a GaO layer, and then, a Zn(CH₃)₂ gas and an O₃ gas) are used to form a ZnO layer. Note that the order of these layers is not limited to this example. A mixed compound layer such as an In—Ga—O layer, an In—Zn—O layer, or a Ga—Zn—O layer may be formed by using these gases. Note that although an H₂O gas that is obtained by bubbling water with an inert gas such as Ar may be used instead of an O₃ gas), it is preferable to use an O₃ gas), which does not contain H.

2-6. Structure Example 4 of Transistor

FIG. 12(A) is a top view of a transistor 300A; FIG. 12(B) is a cross-sectional view taken along dashed-dotted line X1-X2 in FIG. 12(A); and FIG. 12(C) is a cross-sectional view taken along dashed-dotted line Y1-Y2 in FIG. 12(A). Note that in FIG. 12(A), some components of the transistor 300A (e.g., an insulating film functioning as a gate insulating film) are not illustrated to avoid complexity. The direction of the dashed-dotted line X1-X2 may be referred to as a channel length direction, and the direction of the dashed-dotted line Y1-Y2 may be referred to as a channel width direction. As in FIG. 12(A), some components are not illustrated in some cases in top views of transistors described below.

The transistor 300A illustrated in FIG. 12 includes a conductive film 304 over a substrate 302, an insulating film 306 over the substrate 302 and the conductive film 304, an insulating film 307 over the insulating film 306, a metal oxide 308 over the insulating film 307, a conductive film 312 a over the metal oxide 308, and a conductive film 312 b over the metal oxide 308. Over the transistor 300A, specifically, over the conductive films 312 a and 312 b and the metal oxide 308, insulating films 314 and 316, and an insulating film 318 are provided.

In the transistor 300A, the insulating films 306 and 307 function as the gate insulating films of the transistor 300A, and the insulating films 314, 316, and 318 function as protective insulating films of the transistor 300A. Furthermore, in the transistor 300A, the conductive film 304 functions as a gate electrode, the conductive film 312 a functions as a source electrode, and the conductive film 312 b functions as a drain electrode.

In this specification and the like, the insulating films 306 and 307 may be referred to as a first insulating film, the insulating films 314 and 316 may be referred to as a second insulating film, and the insulating film 318 may be referred to as a third insulating film.

The transistor 300A illustrated in FIG. 12 is a channel-etched transistor. The metal oxide of one embodiment of the present invention is suitable for a channel-etched transistor.

2-7. Structure Example 5 of Transistor

FIG. 13(A) is a top view of a transistor 300B; FIG. 13(B) is a cross-sectional view taken along dashed-dotted line X1-X2 in FIG. 13(A); and FIG. 13(C) is a cross-sectional view taken along dashed-dotted line Y1-Y2 in FIG. 13(A).

The transistor 300B illustrated in FIG. 13 includes the conductive film 304 over the substrate 302, the insulating film 306 over the substrate 302 and the conductive film 304, the insulating film 307 over the insulating film 306, the metal oxide 308 over the insulating film 307, the insulating film 314 over the metal oxide 308, the insulating film 316 over the insulating film 314, the conductive film 312 a electrically connected to the metal oxide 308 through an opening 341 a provided in the insulating film 314 and the insulating film 316, and the conductive film 312 b electrically connected to the metal oxide 308 through an opening 341 b provided in the insulating film 314 and the insulating film 316. Over the transistor 300B, specifically, over the conductive films 312 a and 312 b and the insulating film 316, the insulating film 318 is provided.

In the transistor 300B, the insulating films 306 and 307 each function as a gate insulating film of the transistor 300B, the insulating films 314 and 316 each function as a protective insulating film of the metal oxide 308, and the insulating film 318 functions as a protective insulating film of the transistor 300B. Moreover, in the transistor 300B, the conductive film 304 functions as a gate electrode, the conductive film 312 a functions as a source electrode, and the conductive film 312 b functions as a drain electrode.

The transistor 300A illustrated in FIG. 12 has a channel-etched structure, whereas the transistor 300B in FIGS. 13(A), 13(B), and 13(C) has a channel-protective structure. The metal oxide of one embodiment of the present invention is suitable for a channel-protective transistor as well.

2-8. Structure Example 6 of Transistor

FIG. 14(A) is a top view of a transistor 300C; FIG. 14(B) is a cross-sectional view taken along dashed-dotted line X1-X2 in FIG. 14(A); and FIG. 14(C) is a cross-sectional view taken along dashed-dotted line Y1-Y2 in FIG. 14(A).

The transistor 300C illustrated in FIG. 14 is different from the transistor 300B in FIGS. 13(A), 13(B), and 13(C) in the shapes of the insulating films 314 and 316. Specifically, the insulating films 314 and 316 of the transistor 300C have island shapes and are provided over a channel region of the metal oxide 308. Other components are similar to those of the transistor 300B.

2-9. Structure Example 7 of Transistor

FIG. 15(A) is a top view of a transistor 300D; FIG. 15(B) is a cross-sectional view taken along dashed-dotted line X1-X2 in FIG. 15(A); and FIG. 15(C) is a cross-sectional view taken along dashed-dotted line Y1-Y2 in FIG. 15(A).

The transistor 300D illustrated in FIG. 15 includes the conductive film 304 over the substrate 302, the insulating film 306 over the substrate 302 and the conductive film 304, the insulating film 307 over the insulating film 306, the metal oxide 308 over the insulating film 307, the conductive film 312 a over the metal oxide 308, the conductive film 312 b over the metal oxide 308, the insulating film 314 over the metal oxide 308 and the conductive films 312 a and 312 b, the insulating film 316 over the insulating film 314, the insulating film 318 over the insulating film 316, and conductive films 320 a and 320 b over the insulating film 318.

In the transistor 300D, the insulating films 306 and 307 function as first gate insulating films of the transistor 300D, and the insulating films 314, 316, and 318 function as second gate insulating films of the transistor 300D. Furthermore, in the transistor 300D, the conductive film 304 functions as a first gate electrode, the conductive film 320 a functions as a second gate electrode, and the conductive film 320 b functions as a pixel electrode used for a display device. The conductive film 312 a functions as a source electrode, and the conductive film 312 b functions as a drain electrode.

As illustrated in FIG. 15(C), the conductive film 320 b is connected to the conductive film 304 in openings 342 b and 342 c provided in the insulating films 306, 307, 314, 316, and 318. Thus, the same potential is applied to the conductive film 320 b and the conductive film 304.

The structure of the transistor 300D is not limited to that described above, in which the openings 342 b and 342 c are provided so that the conductive film 320 b is connected to the conductive film 304. For example, a structure in which only one of the opening 342 b or the opening 342 c is provided so that the conductive film 320 b is connected to the conductive film 304, or a structure in which the conductive film 320 b is not connected to the conductive film 304 without providing the opening 342 b and the opening 342 c may be employed. Note that in the case where the conductive film 320 b is not connected to the conductive film 304, it is possible to apply different potentials to the conductive film 320 b and the conductive film 304.

The conductive film 320 b is connected to the conductive film 312 b through an opening 342 a provided in the insulating films 314, 316, and 318.

Note that the transistor 300D has the S-channel structure described above.

At least part of this embodiment can be implemented in combination with any of the other embodiments described in this specification as appropriate.

Embodiment 3

In this embodiment, an example of a display panel which can be used for a display portion or the like in a display device including the semiconductor device of one embodiment of the present invention is described with reference to FIG. 17 and FIG. 18 . The display panel described below as an example includes both a reflective liquid crystal element and a light-emitting element and can display an image in both the transmissive mode and the reflective mode. Note that the metal oxide of one embodiment of the present invention and a transistor including the metal oxide can be preferably used in a transistor in a pixel of a display device, a driver for driving the display device, an LSI supplying data to the display device, or the like.

Structure Example of Display Panel

FIG. 17 is a schematic perspective view of a display panel 600 of one embodiment of the present invention. In the display panel 600, a substrate 651 and a substrate 661 are attached to each other. In FIG. 17 , the substrate 661 is denoted by a dashed line.

The display panel 600 includes a display portion 662, a circuit 659, a wiring 666, and the like. The substrate 651 is provided with the circuit 659, the wiring 666, a conductive film 663 that serves as a pixel electrode, and the like. FIG. 17 shows an example in which an IC 673 and an FPC 672 are mounted on the substrate 651. Thus, the structure shown in FIG. 17 can be referred to as a display module including the display panel 600, the FPC 672, and the IC 673.

As the circuit 659, for example, a circuit functioning as a scan line driver circuit can be used.

The wiring 666 has a function of supplying a signal or electric power to the display portion 662 or the circuit 659. The signal or electric power is input to the wiring 666 from the outside through the FPC 672 or from the IC 673.

FIG. 17 shows an example in which the IC 673 is provided on the substrate 651 by a chip on glass (COG) method or the like. As the IC 673, an IC functioning as a scan line driver circuit, a signal line driver circuit, or the like can be used. Note that it is possible that the IC 673 is not provided when, for example, the display panel 600 includes circuits serving as a scan line driver circuit and a signal line driver circuit and when the circuits serving as a scan line driver circuit and a signal line driver circuit are provided outside and a signal for driving the display panel 600 is input through the FPC 672. Alternatively, the IC 673 may be mounted on the FPC 672 by a chip on film (COF) method or the like.

FIG. 17 also shows an enlarged view of part of the display portion 662. The conductive films 663 included in a plurality of display elements are arranged in a matrix in the display portion 662. The conductive film 663 has a function of reflecting visible light and serves as a reflective electrode of a liquid crystal element 640 described later.

As shown in FIG. 17 , the conductive film 663 has an opening. A light-emitting element 660 is positioned closer to the substrate 651 than the conductive film 663 is. Light is emitted from the light-emitting element 660 to the substrate 661 side through the opening in the conductive film 663.

Cross-Sectional Structure Example

FIG. 18 shows an example of cross sections of part of a region including the FPC 672, part of a region including the circuit 659, and part of a region including the display portion 662 of the display panel 600 illustrated in FIG. 17 .

The display panel 600 includes an insulating film 620 between the substrate 651 and the substrate 661. The display panel 600 also includes the light-emitting element 660, a transistor 601, a transistor 605, a transistor 606, a coloring layer 634, and the like between the substrate 651 and the insulating film 620. Furthermore, the display panel 600 includes the liquid crystal element 640, a coloring layer 631, and the like between the insulating film 620 and the substrate 661. The substrate 661 and the insulating film 620 are bonded with an adhesive layer 641. The substrate 651 and the insulating film 620 are bonded with an adhesive layer 642.

The transistor 606 is electrically connected to the liquid crystal element 640 and the transistor 605 is electrically connected to the light-emitting element 660. Since the transistor 605 and the transistor 606 are formed on a surface of the insulating film 620 which is on the substrate 651 side, the transistors 605 and 606 can be formed through the same process.

The substrate 661 is provided with the coloring layer 631, a light-blocking film 632, an insulating film 621, a conductive film 613 serving as a common electrode of the liquid crystal element 640, an alignment film 633 b, an insulating film 617, and the like. The insulating film 617 serves as a spacer for holding a cell gap of the liquid crystal element 640.

Insulating layers such as an insulating film 681, an insulating film 682, an insulating film 683, an insulating film 684, and an insulating film 685 are provided on the substrate 651 side of the insulating film 620. Part of the insulating film 681 functions as a gate insulating layer of each transistor. The insulating film 682, the insulating film 683, and the insulating film 684 are provided to cover each transistor. The insulating film 685 is provided to cover the insulating film 684. The insulating film 684 and the insulating film 685 each function as a planarization layer. Note that an example where the three insulating layers, the insulating film 682, the insulating film 683, and the insulating film 684, are provided to cover the transistors and the like is described here; however, one embodiment of the present invention is not limited to this, and four or more insulating layers, a single insulating layer, or two insulating layers may be provided. The insulating film 684 functioning as a planarization layer is not necessarily provided when not needed.

The transistor 601, the transistor 605, and the transistor 606 each include a conductive film 654 part of which functions as a gate, a conductive film 652 part of which functions as a source or a drain, and a semiconductor film 653. Here, a plurality of layers obtained by processing the same conductive film are shown with the same hatching pattern.

The liquid crystal element 640 is a reflective liquid crystal element. The liquid crystal element 640 has a stacked structure of a conductive film 635, a liquid crystal layer 612, and the conductive film 613. In addition, the conductive film 663 which reflects visible light is provided in contact with the surface of the conductive film 635 that faces the substrate 651. The conductive film 663 includes an opening 655. The conductive film 635 and the conductive film 613 contain a material transmitting visible light. In addition, an alignment film 633 a is provided between the liquid crystal layer 612 and the conductive film 635 and the alignment film 633 b is provided between the liquid crystal layer 612 and the conductive film 613. A polarizing plate 656 is provided on an outer surface of the substrate 661.

In the liquid crystal element 640, the conductive film 663 has a function of reflecting visible light and the conductive film 613 has a function of transmitting visible light. Light entering from the substrate 661 side is polarized by the polarizing plate 656, passes through the conductive film 613 and the liquid crystal layer 612, and is reflected by the conductive film 663. Then, the light passes through the liquid crystal layer 612 and the conductive film 613 again and reaches the polarizing plate 656. In this case, alignment of the liquid crystal is controlled with a voltage that is applied between the conductive film 613 and each of the conductive film 663 and the conductive film 635, and thus optical modulation of light can be controlled. That is, the intensity of light emitted through the polarizing plate 656 can be controlled. Light excluding light in a particular wavelength region is absorbed by the coloring layer 631, and thus, emitted light is red light, for example.

The light-emitting element 660 is a bottom-emission light-emitting element. The light-emitting element 660 has a structure in which a conductive film 643, an EL layer 644, and a conductive film 645 b are stacked in this order from the insulating film 620 side. In addition, a conductive film 645 a is provided to cover the conductive film 645 b. The conductive film 645 b contains a material reflecting visible light, and the conductive film 643 and the conductive film 645 a contain a material transmitting visible light. Light is emitted from the light-emitting element 660 to the substrate 661 side through the coloring layer 634, the insulating film 620, the opening 655, the conductive film 613, and the like.

Here, as illustrated in FIG. 18 , the conductive film 635 transmitting visible light is preferably provided for the opening 655. Accordingly, the liquid crystal is aligned in a region overlapping with the opening 655 as well as in the other regions, in which case an alignment defect of the liquid crystal is prevented from being generated in the boundary portion of these regions and undesired light leakage can be suppressed.

As the polarizing plate 656 provided on an outer surface of the substrate 661, a linear polarizing plate or a circularly polarizing plate can be used. An example of a circularly polarizing plate is a stack including a linear polarizing plate and a quarter-wave retardation plate. Such a structure can reduce reflection of external light. The cell gap, alignment, drive voltage, and the like of the liquid crystal element used as the liquid crystal element 640 are controlled depending on the kind of the polarizing plate so that desirable contrast is obtained.

In addition, an insulating film 647 is provided on the insulating film 646 covering an end portion of the conductive film 643. The insulating film 647 has a function as a spacer for preventing the insulating film 620 and the substrate 651 from getting closer than necessary. In the case where the EL layer 644 or the conductive film 645 a is formed using a blocking mask (metal mask), the insulating film 647 may have a function as a spacer for preventing the blocking mask from being in contact with a surface on which the EL layer 644 or the conductive film 645 a is formed. Note that the insulating film 647 is not necessarily provided when not needed.

One of a source and a drain of the transistor 605 is electrically connected to the conductive film 643 of the light-emitting element 660 through a conductive film 648.

One of a source and a drain of the transistor 606 is electrically connected to the conductive film 663 through a connection portion 607. The conductive film 663 and the conductive film 635 are provided in contact with each other and electrically connected to each other. Here, in the connection portion 607, the conductive layers provided on both surfaces of the insulating film 620 are connected to each other through an opening in the insulating film 620.

A connection portion 604 is provided in a region where the substrate 651 and the substrate 661 do not overlap with each other. The connection portion 604 is electrically connected to the FPC 672 through a connection layer 649. The connection portion 604 has a structure similar to that of the connection portion 607. On the top surface of the connection portion 604, a conductive layer obtained by processing the same conductive film as the conductive film 635 is exposed. Thus, the connection portion 604 and the FPC 672 can be electrically connected to each other through the connection layer 649.

A connection portion 687 is provided in part of a region where the adhesive layer 641 is provided. In the connection portion 687, the conductive layer obtained by processing the same conductive film as the conductive film 635 is electrically connected to part of the conductive film 613 with a connector 686. Accordingly, a signal or a potential input from the FPC 672 connected to the substrate 651 side can be supplied to the conductive film 613 formed on the substrate 661 side through the connection portion 687.

As the connector 686, a conductive particle can be used, for example. As the conductive particle, a particle of an organic resin, silica, or the like coated with a metal material can be used. It is preferable to use nickel or gold as the metal material because contact resistance can be reduced. It is also preferable to use a particle coated with layers of two or more kinds of metal materials, such as a particle coated with nickel and further with gold. As the connector 686, a material capable of elastic deformation or plastic deformation is preferably used. As shown in FIG. 18 , the connector 686 which is the conductive particle has a shape that is vertically crushed in some cases. With the crushed shape, the contact area between the connector 686 and a conductive layer electrically connected to the connector 686 can be increased, thereby reducing contact resistance and suppressing the generation of problems such as disconnection.

The connector 686 is preferably provided so as to be covered with the adhesive layer 641. For example, the connectors 686 are dispersed in the adhesive layer 641 before curing of the adhesive layer 641.

FIG. 18 shows an example of the circuit 659 in which the transistor 601 is provided.

The structure in which the semiconductor film 653 where a channel is formed is provided between two gates is used as an example of the transistor 601 and the transistor 605 in FIG. 18 . One gate is formed using the conductive film 654 and the other gate is formed using a conductive film 623 overlapping with the semiconductor film 653 with the insulating film 682 provided therebetween. Such a structure enables control of threshold voltages of a transistor. In that case, the two gates may be connected to each other and supplied with the same signal to operate the transistor. Such a transistor can have higher field-effect mobility and thus have higher on-state current than other transistors. Consequently, a circuit capable of high-speed operation can be obtained. Furthermore, the area occupied by a circuit portion can be reduced. The use of the transistor having a high on-state current can reduce signal delay in wirings and can reduce display unevenness even in a display panel in which the number of wirings is increased because of increase in size or resolution.

Note that the transistor included in the circuit 659 and the transistor included in the display portion 662 may have the same structure. A plurality of transistors included in the circuit 659 may have the same structure or different structures. A plurality of transistors included in the display portion 662 may have the same structure or different structures.

A material through which impurities such as water and hydrogen do not easily diffuse is preferably used for at least one of the insulating film 682 and the insulating film 683 which cover the transistors. That is, the insulating film 682 or the insulating film 683 can function as a barrier film. Such a structure can effectively suppress diffusion of the impurities into the transistors from the outside, and a highly reliable display panel can be provided.

The insulating film 621 is provided on the substrate 661 side to cover the coloring layer 631 and the light-blocking film 632. The insulating film 621 may have a function as a planarization layer. The insulating film 621 enables the conductive film 613 to have an almost flat surface, resulting in a uniform alignment state of the liquid crystal layer 612.

An example of the method for manufacturing the display panel 600 is described. For example, the conductive film 635, the conductive film 663, and the insulating film 620 are formed in this order over a support substrate provided with a separation layer, and the transistor 605, the transistor 606, the light-emitting element 660, and the like are formed. Then, the substrate 651 and the support substrate are bonded with the adhesive layer 642. After that, separation is performed at the interface between the separation layer and each of the insulating film 620 and the conductive film 635, whereby the support substrate and the separation layer are removed. Separately, the coloring layer 631, the light-blocking film 632, the conductive film 613, and the like are formed over the substrate 661 in advance. Then, the liquid crystal is dropped onto the substrate 651 or the substrate 661 and the substrate 651 and the substrate 661 are bonded with the adhesive layer 641, whereby the display panel 600 can be manufactured.

A material for the separation layer can be selected such that separation at the interface with the insulating film 620 and the conductive film 635 occurs. In particular, it is preferable that a stacked layer of a layer including a high-melting-point metal material, such as tungsten, and a layer including an oxide of the metal material be used as the separation layer, and a stacked layer of a plurality of layers, such as a silicon nitride layer, a silicon oxynitride layer, and a silicon nitride oxide layer, be used as the insulating film 620 over the separation layer. The use of the high-melting-point metal material for the separation layer can increase the formation temperature of a layer formed in a later step, which reduces impurity concentration and achieves a highly reliable display panel.

As the conductive film 635, an oxide or a nitride such as a metal oxide or a metal nitride is preferably used. In the case of using a metal oxide, a material in which at least one of the concentrations of hydrogen, boron, phosphorus, nitrogen, and other impurities and the number of oxygen vacancies is made to be higher than those in a semiconductor layer of a transistor is used for the conductive film 635.

<Components>

The above components will be described below. Note that descriptions of structures having functions similar to those in the above embodiments are omitted.

[Adhesive Layer]

As the adhesive layer, a variety of curable adhesives such as a reactive curable adhesive, a thermosetting adhesive, an anaerobic adhesive, and a photocurable adhesive such as an ultraviolet curable adhesive can be used. Examples of these adhesives include an epoxy resin, an acrylic resin, a silicone resin, a phenol resin, a polyimide resin, an imide resin, a polyvinyl chloride (PVC) resin, a polyvinyl butyral (PVB) resin, and an ethylene vinyl acetate (EVA) resin. In particular, a material with low moisture permeability, such as an epoxy resin, is preferred. Alternatively, a two-component-mixture-type resin may be used. Further alternatively, an adhesive sheet or the like may be used.

Furthermore, the resin may include a drying agent. For example, a substance that adsorbs moisture by chemical adsorption, such as an oxide of an alkaline earth metal (e.g., calcium oxide or barium oxide), can be used. Alternatively, a substance that adsorbs moisture by physical adsorption, such as zeolite or silica gel, may be used. The drying agent is preferably included because it can prevent impurities such as moisture from entering the element, thereby improving the reliability of the display panel.

In addition, it is preferable to mix a filler with a high refractive index or a light-scattering member into the resin, in which case light extraction efficiency can be enhanced. For example, titanium oxide, barium oxide, zeolite, zirconium, or the like can be used.

[Connection Layer]

As the connection layer, an anisotropic conductive film (ACF), an anisotropic conductive paste (ACP), or the like can be used.

[Coloring Layer]

Examples of a material that can be used for the coloring layers include a metal material, a resin material, and a resin material containing a pigment or dye.

[Light-Blocking Layer]

Examples of a material that can be used for the light-blocking layer include carbon black, titanium black, a metal, a metal oxide, and a composite oxide containing a solid solution of a plurality of metal oxides. The light-blocking layer may be a film containing a resin material or a thin film of an inorganic material such as a metal. Stacked films containing the material of the coloring layer can also be used for the light-blocking layer. For example, a stacked-layer structure of a film containing a material of a coloring layer which transmits light of a certain color and a film containing a material of a coloring layer which transmits light of another color can be employed. It is preferable that the coloring layer and the light-blocking layer be formed using the same material because the same manufacturing apparatus can be used and the process can be simplified.

The above is the description of the components.

Manufacturing Method Example

A manufacturing method example of a display panel using a flexible substrate is described.

Here, layers including a display element, a circuit, a wiring, an electrode, optical members such as a coloring layer and a light-blocking layer, an insulating layer, and the like, are collectively referred to as an element layer. The element layer includes, for example, a display element, and may additionally include a wiring electrically connected to the display element or an element such as a transistor used in a pixel or a circuit.

In addition, here, a flexible member which supports the element layer at a stage at which the display element is completed (the manufacturing process is finished) is referred to as a substrate. For example, a substrate includes an extremely thin film with a thickness greater than or equal to 10 nm and less than or equal to 300 μm.

As a method for forming an element layer over a flexible substrate provided with an insulating surface, typically, there are two methods shown below. One of them is to directly form an element layer over the substrate. The other method is to form an element layer over a support substrate that is different from the substrate and then to separate the element layer from the support substrate to be transferred to the substrate. Although not described in detail here, in addition to the above two methods, there is a method in which an element layer is formed over a substrate which does not have flexibility and the substrate is thinned by polishing or the like to have flexibility.

In the case where a material of the substrate can withstand heating temperature in a process for forming the element layer, it is preferable that the element layer be formed directly over the substrate, in which case a manufacturing process can be simplified. At this time, the element layer is preferably formed in a state where the substrate is fixed to the support substrate, in which case transfer thereof in an apparatus and between apparatuses can be easy.

In the case of employing the method in which the element layer is formed over the support substrate and then transferred to the substrate, first, a separation layer and an insulating layer are stacked over the support substrate, and then the element layer is formed over the insulating layer. Next, the element layer is separated from the support substrate and then transferred to the substrate. At this time, selected is a material with which separation at an interface between the support substrate and the separation layer, at an interface between the separation layer and the insulating layer, or in the separation layer occurs. With the method, it is preferable that a material having high heat resistance be used for the support substrate or the separation layer, in which case the upper limit of the temperature applied when the element layer is formed can be increased, and an element layer including a more highly reliable element can be formed.

For example, it is preferable that a stack of a layer containing a high-melting-point metal material, such as tungsten, and a layer containing an oxide of the metal material be used as the separation layer, and a stack of a plurality of layers, such as silicon oxide, silicon nitride, silicon oxynitride, and silicon nitride oxide, be used as the insulating layer over the separation layer.

As the method for separating the support substrate from the element layer, applying mechanical force, etching the separation layer, and making a liquid permeate the separation interface are given as examples. Alternatively, separation may be performed by heating or cooling two layers of the separation interface by utilizing a difference in thermal expansion coefficient.

The separation layer is not necessarily provided in the case where the separation can be performed at an interface between the support substrate and the insulating layer.

For example, glass and an organic resin such as polyimide can be used as the support substrate and the insulating layer, respectively. In that case, a separation trigger may be formed by, for example, locally heating part of the organic resin with laser light or the like, or by physically cutting part of or making a hole through the organic resin with a sharp tool, and separation may be performed at an interface between the glass and the organic resin. As the above-described organic resin, a photosensitive material is preferably used because an opening or the like can be easily formed. The above-described laser light preferably has a wavelength region, for example, from visible light to ultraviolet light. For example, light having a wavelength of greater than or equal to 200 nm and less than or equal to 400 nm, preferably greater than or equal to 250 nm and less than or equal to 350 nm can be used. In particular, an excimer laser having a wavelength of 308 nm is preferably used because the productivity is increased. Alternatively, a solid-state UV laser (also referred to as a semiconductor UV laser), such as a UV laser having a wavelength of 355 nm which is the third harmonic of an Nd:YAG laser, may be used.

Alternatively, a heat-generation layer may be provided between the support substrate and the insulating layer formed of an organic resin, and separation may be performed at an interface between the heat-generation layer and the insulating layer by heating the heat-generation layer. For the heat-generation layer, any of a variety of materials such as a material which generates heat by feeding current, a material which generates heat by absorbing light, and a material which generates heat by applying a magnetic field can be used. For example, for the heat-generation layer, a material selected from a semiconductor, a metal, and an insulator can be used.

In the above-described methods, the insulating layer formed of an organic resin can be used as a substrate after the separation.

The above is the description of a manufacturing method of a flexible display panel.

At least part of this embodiment can be implemented in combination with any of the other embodiments described in this specification as appropriate.

Embodiment 4

In this embodiment, a metal oxide of one embodiment of the present invention is described.

The metal oxide of one embodiment of the present invention includes In (indium), M (M is Al, Ga, Y, or Sn), and Zn (zinc). Specifically, M is preferably Ga (gallium). In the following description, Ga is used as M.

Here, the case where silicon (Si), boron (B), or carbon (C) exists as an impurity in an In—Ga—Zn oxide is described.

<Calculation Model and Calculation Method>

First, calculations were performed using a reference model of an In—Ga—Zn oxide in an amorphous state which has no impurities, a model in which one Si atom is added to the reference model, a model in which one B atom is added to the reference model, and a model in which one C atom is added to the reference model.

Specifically, a model 700 with [In]:[Ga]:[Zn]:[O]=1:1:1:4 shown in FIG. 19(A) was used as the reference crystal model. Note that the model 700 includes 112 atoms.

Strictly, an In-M-Zn oxide having a CAC composition is not in an amorphous state. On the other hand, the In-M-Zn oxide having the CAC composition has lower crystallinity than an In-M-Zn oxide having a CAAC structure. Accordingly, a model in an amorphous state was used for convenience to reduce influence of the crystal structure and observe the bonding state.

In the model 700, a Si atom, a B atom, or a C atom was assumed to exist as an impurity, and one Si atom, one B atom, or one C atom was located in an interstitial site of the model 700. Note that one impurity was added to the model 700 including the 112 atoms. Accordingly, the impurity concentration of the model is approximately 7×10²⁰ [atoms/cm³].

FIG. 20(A) shows a local structure 702 of the vicinity of Si, which is extracted from a model in which the Si atom is bonded to four O atoms in the case where Si exists as an impurity, and FIG. 20(C) shows a local structure 704 of the vicinity of Si, which is extracted from a model in which the Si atom is bonded to three O atoms and one Ga atom.

FIG. 21(A) shows a local structure 706 of the vicinity of a B atom, which is extracted from a model in which the B atom is bonded to three O atoms in the case where B exists as an impurity, and FIG. 21(C) shows a local structure 708 of the vicinity of B, which is extracted from the model.

FIG. 22(A) shows a local structure 710 of the vicinity of a C atom, which is extracted from a model in which the C atom is bonded to two O atoms and one Ga atom in the case where C exists as an impurity, and FIG. 22(C) shows a local structure 712 of the vicinity of a C atom, which is extracted from a model in which the C atom is bonded to one O atom and one Ga atom.

The specific calculation is as follows. A first principle electronic state calculation package, VASP (Vienna Ab initio Simulation Package), was used for the atomic relaxation calculation. The calculation conditions are listed in the following table.

TABLE 1 Software VASP Exchange-correlation functional GGA-PBE Pseudopotential PAW method Cut-off energy of plane wave 800 ev Sampling Structure optimization 1 × 1 × 1 point k Density of states 2 × 2 × 2

<Density of States>

FIG. 19(B) shows the density of states in FIG. 19(A). In FIG. 19(B), the Fermi level (the energy of the highest occupied level of electrons) is adjusted to be 0 eV in the horizontal axis. It was found from FIG. 19(B) that the electrons reach the valence band maximum and the level in the gap does not exist.

FIG. 20(B) and FIG. 20(D) show the density of states in the case where one Si atom is added as an impurity. Note that FIG. 20(B) shows the density of states in the case where the local structure 702 shown in FIG. 20(A) is included. FIG. 20(D) shows the density of states in the case where the local structure 704 shown in FIG. 20(C) is included.

It was found from FIG. 20(B) and FIG. 20(D) that when a Si atom exists, the Fermi level is located in the conduction band. This indicates that carriers are generated in an In—Ga—Zn oxide (the In—Ga—Zn oxide is made to be an n-type) owing to Si atoms.

FIG. 21(B) and FIG. 21(D) show the density of states in the case where one B atom is added as an impurity. Note that FIG. 21(B) shows the density of states in the case where the local structure 706 shown in FIG. 21(A) is included. FIG. 21(D) shows the density of states in the case where the local structure 708 shown in FIG. 21(C) is included.

It was found from FIG. 21(B) and FIG. 21(D) that when a B atom exists, the Fermi level is located in the conduction band. This indicates that carriers are generated in an In—Ga—Zn oxide (the In—Ga—Zn oxide is made to be an n-type) owing to B atoms.

FIG. 22(B) and FIG. 22(D) show the density of states in the case where one C atom is added as an impurity. Note that FIG. 22(B) shows the density of states in the case where the local structure 710 shown in FIG. 22(A) is included. FIG. 22(D) shows the density of states in the case where the local structure 712 shown in FIG. 22(C) is included.

It was found from FIG. 22(B) and FIG. 22(D) that when a C atom exists, the Fermi level is located in the conduction band. This indicates that carriers are generated in an In—Ga—Zn oxide (the In—Ga—Zn oxide is made to be an n-type) owing to C atoms.

It is highly probable that Si atoms and B atoms exist as cations in an In—Ga—Zn oxide because the electronegativities of Si and B are closer to the electronegativities of In, Ga, and Zn than the electronegativity of O. Thus, it is supposed that carriers are generated.

Although C is bonded to a metal and O because the electronegativity of C is between the electronegativity of O and the electronegativities of In, Ga, and Zn, it is assumed that C is likely to exist as cations basically.

Furthermore, a Si atom, a B atom, and a C atom are more strongly bonded to an O atom than an In atom, a Ga atom, and a Zn atom are. For that reason, by the entry of a Si atom, a B atom, and a C atom, O atoms bonded to an In atom, a Ga atom, and a Zn atom are trapped by the Si atom, the B atom, and the C atom. It is thus presumed that deep levels corresponding to oxygen vacancies are formed.

The structure and method described in this embodiment can be implemented by being combined as appropriate with any of the other structures and methods described in the other embodiments.

Example 1

In this example, a metal oxide of one embodiment of the present invention, which was formed over a substrate, was measured with a variety of methods, and the measurement results are described. Note that in this example, Sample 1A, Sample 1B, Sample 1C, Sample 1D, Sample 1E, Sample 1F, Sample 1G, Sample 1H, and Sample 1J, and Sample 1X, Sample 1Y, and Sample 1Z were fabricated.

<Structure of Samples and Fabrication Method Thereof

Sample 1A, Sample 1B, Sample 1C, Sample 1D, Sample 1E, Sample 1F, Sample 1G, Sample 1H, and Sample 1J, and Sample 1X, Sample 1Y, and Sample 1Z relating to one embodiment of the present invention will be described below. Sample 1A to Sample 1J and Sample 1X to Sample 1Z each include a substrate and a metal oxide over the substrate. Note that Sample 1A to Sample 1J are different from Sample 1X to Sample 1Z in the thickness of the metal oxide.

A 100-nm-thick metal oxide film was formed for Sample 1A to Sample 1J. Sample 1A to Sample 1J were fabricated at different temperatures and different oxygen flow rate ratios in formation of the metal oxide film.

Meanwhile, a 500-nm-thick metal oxide film was formed for Sample 1X to Sample 1Z. Sample 1X to Sample 1Z were fabricated at different temperatures and different oxygen flow rate ratios in formation of the metal oxide film.

The temperatures and the oxygen flow rate ratios in formation of the metal oxide films of Sample 1A to Sample 1J and Sample 1X to Sample 1Z are shown in the following table.

TABLE 2 O₂ Formation Film Flow rate [sccm] ratio temperature thickness O₂ Ar [%] [° C.] [nm] Sample 1A 30 270 10 R.T. 100 Sample 1B 90 210 30 R.T. 100 Sample 1C 300 0 100 R.T. 100 Sample 1D 30 270 10 130 100 Sample 1E 90 210 30 130 100 Sample 1F 300 0 100 130 100 Sample 1G 30 270 10 170 100 Sample 1H 90 210 30 170 100 Sample 1J 300 0 100 170 100 Sample 1X 30 270 10 R.T. 500 Sample 1Y 30 270 10 130 500 Sample 1Z 300 0 100 170 500

Next, methods for fabricating the samples will be described.

A glass substrate was used as the substrate. Over the substrate, an In—Ga—Zn oxide was formed as a metal oxide with a sputtering apparatus. The formation conditions were as follows: the pressure in a chamber was 0.6 Pa; and a metal oxide target (an atomic ratio of In:Ga:Zn=4:2:4.1) was used as a target. The metal oxide target provided in the sputtering apparatus was supplied with an AC power of 2500 W, so that the metal oxide film was formed.

The formation temperatures and oxygen flow rate ratios shown in the above table were used as the conditions for forming metal oxide films to fabricate Sample 1A to Sample 1J and Sample 1X to Sample 1Z.

Through the above steps, Sample 1A to Sample 1J and Sample 1X to Sample 1Z were fabricated.

<Analysis by X-Ray Photoelectron Spectroscopy Measurement>

In this section, the results of X-ray photoelectron spectroscopy (XPS) measurement performed on Sample 1A, Sample 1D, and Sample 1J are described. Note that the measurement was performed using Quantera SXM manufactured by PHI, Inc. The conditions were as follows: an X-ray source was monochromatic Al (1486.6 eV), a detected region was a circle with a diameter of 100 μm, and the detection depth was greater than or equal to 4 nm and less than or equal to 5 nm at an extraction angle of 45°. In the measurement spectrum, an In3d5/2 peak, a Ga3d peak, a Zn3p peak, and an O1s peak were detected as correction references. The proportion of each kind of atoms [atomic %] was calculated on the basis of the detected peaks.

FIG. 23 shows XPS analysis results. Note that pie charts shown in FIG. 23 were normalized on the assumption that the atomic ratio of In was 4.

As shown in FIG. 23 , neither the atomic ratio of Ga nor that of Zn was an integer in the case where the charts were normalized on the assumption that the atomic ratio of In was an integer. Thus, it was found that the atomic ratios of Ga and Zn were non-integers in the case where the charts were normalized on the assumption that the atomic ratio of In was an integer.

It was also found that, in Sample 1A, Sample 1D, and Sample 1J, the atomic ratio of Ga in the formed metal oxide film was less than that of Ga in the metal oxide used as the target. In Sample 1J, the atomic ratio of Zn in the formed metal oxide film was [Zn]=3.21, which was less than the atomic ratio of Zn, [Zn]=4.1 in the metal oxide used as the target. Furthermore, in Sample 1J, which was formed at the highest temperature, the ratio of Zn in the formed metal oxide film tended to be smaller than that in Sample 1A and Sample 1D, which were formed at lower temperatures than Sample 1J. This is probably because Zn was volatilized when the film was formed while being heated.

<Analysis by X-Ray Diffraction>

In this section, results of X-ray diffraction (XRD) measurement performed on the metal oxides over the glass substrates will be described.

First, XRD analysis was performed on Sample 1A to Sample 1J by a powder method. As an XRD apparatus, D8 ADVANCE manufactured by Bruker AXS GmbH was used. The conditions were as follows: scanning was performed by an out-of-plane method at θ/2θ; the scanning range was 15 deg. to 50 deg.; the step width was 0.01 deg.; and the accumulation time per point was 0.1 sec.

FIG. 24 shows XRD spectra measured by an out-of-plane method. Note that the vertical axis represents intensity [a. u], and the horizontal axis represents an angle 2θ [deg.].

In the XRD spectra shown in FIG. 24 , the higher the substrate temperature at the time of film formation is or the higher the oxygen gas flow rate ratio at the time of film formation is, the higher the intensity of the peak at around 2θ=31° is (in this example, greater than or equal to 30° and less than or equal to 32°). Note that the peak at around 2θ=31° is known to be derived from a crystalline IGZO compound whose c-axes are aligned in a direction substantially perpendicular to a formation surface or a top surface of the crystalline IGZO compound (such a compound is also referred to as CAAC-IGZO).

Also in the XRD spectra in FIG. 24 , as the substrate temperature at the time of film formation is lower or the oxygen gas flow rate ratio at the time of film formation is lower, a peak at around 2θ=31° becomes less clear. Accordingly, it was found that there were no alignment in the a-b plane direction and c-axis alignment in the measured areas of the samples that were formed at a lower substrate temperature or with a lower oxygen gas flow rate ratio.

Here, in order to further analyze the metal oxide film formed under the conditions of Sample 1A, Sample 1D, and Sample 1J, XRD analysis was performed on Sample 1X, Sample 1Y, and Sample 1Z by a grazing incidence XRD method (thin film method).

Note that SmartLab manufactured by Rigaku Corporation was used as the XRD apparatus. FIG. 25 shows a schematic view and setting of the apparatus. The output was set to 45 kV and 200 mA (a rotating anticathode), and monochromatic X-ray was obtained with a Ge (220) monochrometer. The incident slit, the longitudinal slit, and the incident angle were set to 0.1 mm, 10 mm, and 0.5 deg., respectively. Alight-receiving slit 1 and a light-receiving slit 2 were opened, and a light-receiving solar slit was set to 0.5 deg.

As the measurement conditions, scanning was performed by an out-of-plane method at 2θ/ω with an accumulation time per point of 100 sec. Here, the step width was set to 0.1 deg. in the scanning range of 5 deg. to 45 deg. The step width was set to 0.2 deg. in the scanning range of 45 deg. to 110 deg.

FIG. 26 shows the measurement results of XRD spectra. Note that the vertical axis represents intensity [a. u], and the horizontal axis represents an angle 2θ [deg.]. Note that in this specification, the maximum peak intensity is referred to as a peak intensity in some cases.

As shown in FIG. 26 , the peak intensity was detected between 2θ=31° and 2θ=34° in Sample 1Z, Sample 1Y, and Sample 1X. Also in the XRD spectra in FIG. 26 , the highest peak intensity at around 2θ=31° was detected in Sample 1Z, followed by Sample 1Y and Sample 1X. Note that the peak at around 2θ=34° (in this example, greater than or equal to 33° and less than or equal to 35°) is known to be derived from a metal oxide including a nanocrystal (in particular, in the case where such a metal oxide has a function similar to that of a semiconductor, it is referred to as a nanocrystalline oxide semiconductor, hereinafter referred to as an nc-OS).

FIG. 26 shows the peak intensity detected between 2θ=31° and 2θ=34° in Sample 1Z, Sample 1Y, and Sample 1X and asymmetric diffraction with the angle at which the peak intensity was detected as the symmetry axis.

FIG. 27 and FIG. 28 show the measurement results of XRD spectrum of each of Sample 1Z, Sample 1Y, Sample 1X, and quartz glass as a comparative example. FIG. 27(A) and FIG. 27(B) show the measurement results of Sample 1Y, FIG. 27(C) and FIG. 27(D) show the measurement results of Sample 1Z, FIG. 28(A) and FIG. 28(B) show the measurement results of quartz glass, and FIG. 28(C) and FIG. 28(D) show the measurement results of Sample 1X. Note that FIG. 27(B), FIG. 27(D), FIG. 28(B), and FIG. 28(D) are enlarged views of regions denoted by dotted lines in FIG. 27(A), FIG. 27(C), FIG. 28(A), and FIG. 28(C), respectively.

Here, the peak intensity between 2θ=31° and 2θ=34° was detected probably because of the synthesis of a peak of a crystalline IGZO compound whose peak intensity is detected at 2θ=31° and a peak of a metal oxide (nc-OS) including a nanocrystal, whose peak intensity is detected at 2θ=34°. Thus, Sample 1Z and Sample 1Y are presumed to include the crystalline IGZO compound whose peak intensity is detected at 2θ=31° and the metal oxide (nc-OS) including a nanocrystal, whose peak intensity is detected at 2θ=34°.

In Sample 1Z and Sample 1Y, the proportion of the metal oxide (nc-OS) including a nanocrystal is lower than that of the crystalline IGZO compound, which probably results in the peak whose intensity is close to 2θ=31° and which has a broader width toward 2θ=34°. Furthermore, Sample 1Z has a higher proportion of the crystalline IGZO compound than Sample 1Y, and thus, the peak intensity of Sample 1Z was probably detected at closer to 2θ=31° than the peak intensity of Sample 1Y.

Meanwhile, in the measurement results of Sample 1X shown in FIG. 28(C) and FIG. 28(D), the peak intensity was detected at around 2θ=34° and asymmetric diffraction with the angle at which the peak intensity was detected as the symmetry axis was obtained. Sample 1A, which was formed under the same formation condition of the metal oxide film as Sample 1X, did not have a clear peak in the XRD spectrum shown in FIG. 24 . That is, Sample 1X as well as Sample 1A is not presumed to have a clear peak derived from orientation in the a-b plane direction and the c-axis direction in the measured area. In other words, Sample 1X is probably a metal oxide with low crystallinity.

As a comparative sample, the measurement results of quartz glass having no crystallinity are shown in FIG. 28(A) and FIG. 28(B). The measurement results of quartz glass show the peak intensity detected at around 2θ=21° and symmetric diffraction with the angle at which the peak intensity was detected as the axis.

Meanwhile, unlike quartz glass, Sample 1X, which was considered to have low crystallinity, showed asymmetric diffraction with the angle at which the peak intensity of the XRD spectrum was detected as the symmetry axis. Thus, Sample 1X probably has a structure different from that of quartz glass.

It was thus found that the peak intensity was detected between 2θ=31° and 2θ=34° in the XRD spectra of the metal oxide including the crystalline IGZO compound and the metal oxide including a nanocrystal (nc-OS), and asymmetric diffraction with the angle at which the peak intensity was detected as the symmetry axis was obtained. It was also found that the metal oxide formed at a low substrate temperature or with a low oxygen gas flow rate ratio had asymmetric diffraction with the angle at which the peak intensity of the XRD spectrum was detected as the symmetry axis, and had a structure different from that of quartz glass.

<TEM Images and Electron Diffraction>

This section describes the observation and analysis results of Sample 1A, Sample 1D, and Sample 1J with a high-angle annular dark field scanning transmission electron microscope (HAADF-STEM) (hereinafter, an image obtained with a HAADF-STEM is also referred to as a TEM image).

This section also describes electron diffraction patterns obtained by irradiation of Sample 1A, Sample 1D, and Sample 1J with an electron beam with a probe diameter of 1 nm (also referred to as a nanobeam electron beam).

The plan-view TEM images were observed with a spherical aberration corrector function. The HAADF-STEM images were obtained using an atomic resolution analytical electron microscope JEM-ARM200F manufactured by JEOL Ltd. under the following conditions: the acceleration voltage was 200 kV; and irradiation with an electron beam with a diameter of approximately 0.1 nmφ was performed.

Note that the electron diffraction patterns were observed while an electron beam irradiation was performed at a constant rate from 0 second to 35 seconds.

FIG. 29(A) shows a cross-sectional TEM image of Sample 1A, and FIG. 29(B) shows an electron diffraction pattern of Sample 1A. FIG. 29(C) shows a cross-sectional TEM image of Sample 1D, and FIG. 29(D) shows an electron diffraction pattern of Sample 1D. FIG. 29(E) shows a cross-sectional TEM image of Sample 1J, and FIG. 29(F) shows an electron diffraction pattern of Sample 1J.

It is known that, for example, when an electron beam with a probe diameter of 300 nm is incident on a CAAC-OS including an InGaZnO₄ crystal in a direction parallel to the sample surface, a diffraction pattern including a spot derived from the (009) plane of the InGaZnO₄ crystal is obtained. That is, the CAAC-OS has c-axis alignment and the c-axes are aligned in the direction substantially perpendicular to the formation surface or the top surface of the CAAC-OS. Meanwhile, a ring-like diffraction pattern is shown when an electron beam with a probe diameter of 300 nm is incident on the same sample in a direction perpendicular to the sample surface. That is, it is found that the CAAC-OS has neither a-axis alignment nor b-axis alignment.

Furthermore, a diffraction pattern like a halo pattern is observed when a metal oxide including a nanocrystal (in particular, in the case where such a metal oxide has a function similar to that of a semiconductor, it is referred to as a nanocrystalline oxide semiconductor (nc-OS)) is subjected to electron diffraction using an electron beam with a large probe diameter (e.g., 50 nm or larger). Meanwhile, bright spots are observed in a nanobeam electron diffraction pattern of the metal oxide including a nanocrystal found using an electron beam with a small probe diameter (e.g., smaller than 50 nm). Furthermore, in a nanobeam electron diffraction pattern of the metal oxide including a nanocrystal, a region with high luminance in a circular (ring) pattern is shown in some cases. In addition, a plurality of bright spots are shown in a ring-like shape in some cases.

A nanocrystal (hereinafter, also referred to as nc) was found in Sample 1A from the result of the cross-sectional TEM observation as shown in FIG. 29(A). As shown in FIG. 29(B), the observed electron diffraction pattern of Sample 1A has a region with high luminance in a circular (ring) pattern. Furthermore, a plurality of spots were observed in the ring-shaped region.

Sample 1D was found to have a CAAC structure and a nanocrystal from the result of the cross-sectional TEM observation shown in FIG. 29(C). As shown in FIG. 29(D), the observed electron diffraction pattern of Sample 1D has a region with high luminance in a circular (ring) pattern. Furthermore, a plurality of spots were observed in the ring-shaped region. In the diffraction pattern, spots derived from the (009) plane were slightly observed.

Meanwhile, Sample 1J was clearly found to have layered arrangement of a CAAC structure from the result of the cross-sectional TEM observation in FIG. 29(E). Furthermore, spots derived from the (009) plane were clearly observed from the result of the electron diffraction pattern of Sample 1J shown in FIG. 29(F).

The features observed in the cross-sectional TEM images and the plan-view TEM images are one aspect of a structure of a metal oxide.

Next, electron diffraction patterns obtained by irradiation of Sample 1A with an electron beam with a probe diameter of 1 nm (also referred to as a nanobeam electron beam) are shown in FIG. 30 .

Electron diffraction patterns of a black dot a1, a black dot a2, a black dot a3, a black dot a4, and a black dot a5 in the plan-view TEM image of Sample 1A in FIG. 30(A) were observed. Note that the electron diffraction patterns were observed while electron beam irradiation was performed at a constant rate from 0 second to 35 seconds. FIG. 30(C), FIG. 30(D), FIG. 30(E), FIG. 30(F), and FIG. 30(G) show the results of the black dot a1, the black dot a2, the black dot a3, the black dot a4, and the black dot a5, respectively.

In FIG. 30(C), FIG. 30(D), FIG. 30(E), FIG. 30(F), and FIG. 30(G), regions with high luminance in a ring pattern were observed. Furthermore, a plurality of spots were observed in the ring-shaped regions.

Electron diffraction patterns of a black dot b1, a black dot b2, a black dot b3, a black dot b4, and a black dot b5 in the cross-sectional TEM image of Sample 1A in FIG. 30(B) are observed. FIG. 30(H), FIG. 30(I), FIG. 30(J), FIG. 30(K), and FIG. 30(L) show the results of the black dot b1, the black dot b2, the black dot b3, the black dot b4, and the black dot b5, respectively.

In FIG. 30(H), FIG. 30(I), FIG. 30(J), FIG. 30(K), and FIG. 30(L), regions with high luminance in a ring pattern were observed. Furthermore, a plurality of spots were observed in the ring-shaped regions.

That is, it was found that Sample 1A had an nc structure and had characteristics distinctly different from those of a metal oxide having an amorphous structure and those of a metal oxide having a single crystal structure.

As described above, the electron diffraction patterns of Sample 1A and Sample 1D each have a region with high luminance in a ring pattern and a plurality of bright spots appeared in the ring-shaped region. It was thus found that Sample 1A exhibits an electron diffraction pattern of the metal oxide including nanocrystals and does not show alignment in the plane direction and the cross-sectional direction. Sample 1D was found to be a mixed material of the nc structure and the CAAC structure.

Meanwhile, the electron diffraction pattern of Sample 1J includes spots derived from the (009) plane of an InGaZnO₄ crystal. It was thus found that Sample 1J had c-axis alignment and the c-axes were aligned in the direction substantially perpendicular to the formation surface or the top surface of Sample 1J.

<Analysis of TEM Image>

This section describes the observation and analysis results of Sample 1A, Sample 1C, Sample 1D, Sample 1F, and Sample 1G with an HAADF-STEM.

The results of image analysis of plan-view TEM images are described. The plan-view TEM images were obtained with a spherical aberration corrector function. The plan-view TEM images were obtained using an atomic resolution analytical electron microscope JEM-ARM200F manufactured by JEOL Ltd. under the following conditions: the acceleration voltage was 200 kV; and irradiation with an electron beam with a diameter of approximately 0.1 nmφ was performed.

FIG. 31 shows the plan-view TEM images of Sample 1A, Sample 1C, Sample 1D, Sample 1F, Sample 1G, and Sample 1J and images obtained through image processing of the plan-view TEM images. Note that in a table in FIG. 31 , left views are the plan-view TEM images and right views are the images obtained through image processing of the plan-view TEM images on the left side.

Image processing and image analyzing methods are described. First, as image processing, the plan-view TEM image in FIG. 31 was subjected to fast Fourier transform (FFT), so that an FFT image was obtained. Then, the obtained FFT image was subjected to mask processing except for a range from 2.8 nm⁻¹ to 5.0 nm⁻¹. After that, the FFT image subjected to mask processing was subjected to inverse fast Fourier transform (IFFT) to obtain an FFT filtering image.

To conduct the image analysis, first, lattice points were extracted from the FFT filtering image. The extraction of lattice points was performed in the following manner. First, noise in the FFT filtering image was removed. To remove the noise, the luminance of a region within a 0.05-nm radius was smoothed using the following formula.

$\begin{matrix} \left\lbrack {{Formula}1} \right\rbrack &  \\ {{{S\_{Int}}\left( {x,y} \right)} = {\sum\limits_{r \leq 0.05}\frac{{Int}\left( {x^{\prime},y^{\prime}} \right)}{r}}} & (1) \end{matrix}$

Here, S_Int(x,y) represents the smoothed luminance at the coordinates (x,y), r represents the distance between the coordinates (x,y) and the coordinates (x′,y′), and Int(x′,y′) represents the luminance at the coordinates (x′,y′). In the calculation, r is regarded as 1 when it is 0.

Then, a search for lattice points was conducted. The coordinates with the highest luminance among candidate lattice points within a 0.22-nm radius were regarded as the lattice point. At this point, a candidate lattice point was extracted. Within a 0.22-nm radius, detection errors of lattice points due to noise can be less frequent. Note that adjacent lattice points are a certain distance away from each other in the TEM image; thus, two or more lattice points are unlikely to be observed within a 0.22-nm radius.

Subsequently, coordinates with the highest luminance within a 0.22-nm radius from the extracted candidate lattice point were extracted to redetermine a candidate lattice point. The extraction of a candidate lattice point was repeated in this manner until no new candidate lattice point appeared; the coordinates at that point were determined as lattice points. Similarly, determination of another lattice point was performed at a position 0.22 nm or more away from the determined lattice point; thus, lattice points were determined in the entire region. The determined lattice points are collectively called a lattice point group.

Next, a method for deriving an orientation of a hexagonal lattice from the extracted lattice point group is described with reference to schematic diagrams in FIG. 32(A), FIGS. 32(B), and 32(C) and a flow chart in FIG. 32(D). First, a reference lattice point was determined and the six closest lattice points to the reference lattice point were connected to form a hexagonal lattice (see FIG. 32(A) and Step S101 in FIG. 32(D)). After that, an average distance R between the reference lattice point, which was the center point of the hexagonal lattice, and each of the lattice points, which is a vertex, was calculated. Then, a regular hexagon was formed with the use of the reference lattice point as the center point and the calculated distance R as the distance from the center point to each vertex (see FIG. 32(B) and Step S102 in FIG. 32(D)). The distances from the vertices of the regular hexagon to their respective closest lattice points were regarded as a distance d1, a distance d2, a distance d3, a distance d4, a distance d5, and a distance d6 (see Step S103 in FIG. 32(D)). Next, the regular hexagon was rotated around the center point through 60° by 0.1°, and the average deviation between the hexagonal lattice and the rotated regular hexagon [D=(d1+d2+d3+d4+d5+d6)/6] was calculated (see Step S104 in FIG. 32(D)). Then, a rotation angle θ of the regular hexagon when the average deviation D becomes minimum was calculated as the orientation of the hexagonal lattice (see FIG. 32(C) and Step S105 in FIG. 32(D)).

Next, an observation area of the plan-view TEM image was adjusted so that hexagonal lattices whose orientations were 30° account for the highest percentage. Here, the average orientation of hexagonal lattice within a 1-nm radius was calculated. The plan-view TEM image obtained through image processing was then shown in such a manner that color or gradation changes in accordance with the angle of the hexagonal lattice in the region. The image obtained through image processing of the plan-view TEM image in FIG. 31 is an image obtained by performing image analysis on the plan-view TEM image in FIG. 31 by the above method and applying gradation in accordance with the angle of the hexagonal lattice. In other words, the image obtained through the image processing of the plan-view TEM image is an image in which the orientations of lattice points in certain wavenumber ranges are extracted by color-coding the certain wavenumber ranges in an FFT filtering image of the plan-view TEM image.

As shown in FIG. 31 , in Sample 1A and Sample 1D in which nc was observed, the hexagons were oriented randomly and distributed in a mosaic pattern. In Sample 1J in which a layered structure was observed in the cross-sectional TEM image, regions with uniformly oriented hexagons exist in a large area of several tens of nanometers. It was found that Sample 1D included an nc region in a random mosaic pattern and a large-area region with uniform orientation as in Sample 1J.

It was found from FIG. 31 that as the substrate temperature at the time of film formation is lower or the oxygen gas flow rate ratio at the time of film formation is lower, regions in which the hexagons are oriented randomly and distributed in a mosaic pattern are likely to exist.

Through the analysis of a plan-view TEM image of a CAAC-OS, a boundary portion where angles of hexagonal lattices change can be examined.

Next, Voronoi diagrams were formed using lattice point groups in Sample 1A. A Voronoi diagram is an image partitioned by regions including a lattice point group. Each lattice point is closer to regions surrounding the lattice point than to any other lattice point. A method for forming a Voronoi diagram is described below in detail using schematic diagrams in FIG. 33(A), FIG. 33(B), FIG. 33(C), and FIG. 33(D) and a flow chart in FIG. 33(E).

First, a lattice point group was extracted by the method shown in FIG. 32 and the like (see FIG. 33(A) and Step S111 in FIG. 33(E)). Next, adjacent lattice points were connected with segments (see FIG. 33(B) and Step S112 in FIG. 33(E)). Then, perpendicular bisectors of the segments were drawn (see FIG. 33(C) and Step S113 in FIG. 33(E)). Subsequently, points where three perpendicular bisectors intersect were extracted (see Step S114 in FIG. 33(E)). The points are called Voronoi points. After that, adjacent Voronoi points were connected with segments (see FIG. 33(D) and Step S115 in FIG. 33(E)). A polygonal region surrounded by the segments at this point is called a Voronoi region. In the above method, a Voronoi diagram was formed.

FIG. 34 shows the proportions of the shapes of Voronoi regions (any of tetragon to enneagon) in Sample 1A, Sample 1C, Sample 1D, Sample 1F, Sample 1G, and Sample 1J. Bar graphs show the numbers of the shapes of Voronoi regions (any of tetragon to enneagon) in the samples. Furthermore, tables show the proportions of the shapes of Voronoi regions (any of tetragon to enneagon) in the samples.

It was found from FIG. 34 that the proportion of hexagons was likely to be high in Sample 1J with a high degree of crystallinity and the proportion of hexagons was likely to be low in Sample 1A with a low degree of crystallinity. The proportion of hexagons in Sample 1D was between that in Sample 1J and that of Sample 1A. Accordingly, it was found from FIG. 34 that the crystal state of the metal oxide significantly differs under different formation conditions.

It was found from FIG. 34 that as the substrate temperature at the time of film formation is lower or the oxygen gas flow rate ratio at the time of film formation is lower, the degree of crystallinity is lower and the proportion of hexagons is lower.

<Elementary Analysis>

This section describes the analysis results of elements included in Sample 1A. For the analysis, by energy dispersive X-ray spectroscopy (EDX), EDX mapping images are obtained and evaluated. An energy dispersive X-ray spectrometer Analysis Station JED-2300T manufactured by JEOL Ltd. is used as an elementary analysis apparatus in the EDX measurement. A Si drift detector is used to detect an X-ray emitted from the sample.

In the EDX measurement, an EDX spectrum of a point is obtained in such a manner that electron beam irradiation is performed on the point in a detection target region of a sample, and the energy of characteristic X-ray of the sample generated by the irradiation and its frequency are measured. In this example, peaks of an EDX spectrum of the point are attributed to electron transition to the L shell in an In atom, electron transition to the K shell in a Ga atom, and electron transition to the K shell in a Zn atom and the K shell in an O atom, and the proportions of the atoms in the point are calculated. An EDX mapping image indicating distributions of proportions of atoms can be obtained through the process in an analysis target region of a sample.

FIG. 35 shows a cross-sectional TEM image, a plan-view TEM image, and EDX mapping images of Sample 1A. In the EDX mapping images, the proportion of an element is indicated by grayscale: the more measured elements exist in a region, the brighter the region is; the less measured elements exist in a region, the darker the region is. The magnification of the EDX mapping images in FIG. 35 is 7,200,000 times.

FIG. 35(A) shows a cross-sectional TEM image, and FIG. 35(E) shows a plan-view TEM image. FIG. 35(B) shows a cross-sectional EDX mapping image of In atoms, and FIG. 35(F) shows a plan-view EDX mapping image of In atoms. In the EDX mapping image in FIG. 35(B), the proportion of the In atoms in all the atoms is the range of 9.28 to 33.74 [atomic %]. In the EDX mapping image in FIG. 35(F), the proportion of the In atoms in all the atoms is in the range of 12.97 to 38.01 [atomic %].

FIG. 35(C) shows a cross-sectional EDX mapping image of Ga atoms, and FIG. 35(G) shows a plan-view EDX mapping image of Ga atoms. In the EDX mapping image in FIG. 35(C), the proportion of the Ga atoms in all the atoms is in the range of 1.18 to 18.64 [atomic %]. In the EDX mapping image in FIG. 35(G), the proportion of the Ga atoms in all the atoms is in the range of 1.72 to 19.82 [atomic %].

FIG. 35(D) shows a cross-sectional EDX mapping image of Zn atoms, and FIG. 35(H) shows a plan-view EDX mapping image of Zn atoms. In the EDX mapping image in FIG. 35(D), the proportion of the Zn atoms in all the atoms is in the range of 6.69 to 24.99 [atomic %]. In the EDX mapping image in FIG. 35(H), the proportion of the Zn atoms in all the atoms is in the range of 9.29 to 28.32 [atomic %].

Note that FIG. 35(A), FIG. 35(B), FIG. 35(C), and FIG. 35(D) show the same region in the cross section of Sample 1A. FIG. 35(E), FIG. 35(F), FIG. 35(G), and FIG. 35(H) show the same region in the plane of Sample 1A.

FIG. 36 shows enlarged cross-sectional EDX mapping images and enlarged plan-view EDX mapping images of Sample 1A. FIG. 36(A) is an enlarged view of a part in FIG. 35(B). FIG. 36(B) is an enlarged view of a part in FIG. 35(C). FIG. 36(C) is an enlarged view of a part in FIG. 35(D). FIG. 36(D) is an enlarged view of a part in FIG. 35(F). FIG. 36(E) is an enlarged view of a part in FIG. 35(G). FIG. 36(F) is an enlarged view of a part in FIG. 35(H).

The EDX mapping images in FIG. 36(A), FIG. 36(B), and FIG. 36(C) show relative distribution of bright and dark areas, indicating that the atoms have distributions in Sample 1A. Areas surrounded by solid lines and areas surrounded by dashed lines in FIG. 36(A), FIG. 36(B), and FIG. 36(C) were focused on.

As shown in FIG. 36(A), a relatively bright region occupies a large area in the area surrounded by the solid line and a relatively dark region occupies a large area in the area surrounded by the dashed line. As shown in FIG. 36(B), a relatively dark region occupies a large area in the area surrounded by the solid line and a relatively bright region occupies a large area in the area surrounded by the dashed line.

That is, it was found that the areas surrounded by the solid lines were regions including a relatively large number of In atoms and the areas surrounded by the dashed lines were regions including a relatively small number of In atoms. FIG. 36(C) shows that a lower portion of the area surrounded by the solid line is relatively bright and an upper portion thereof is relatively dark. Thus, it was found that the area surrounded by the solid line was a region including In_(X2)Zn_(Y2)O_(Z2), InO_(X1), or the like as a main component.

It was also found that the area surrounded by the solid line was a region including a relatively small number of Ga atoms and the area surrounded by the dashed line was a region including a relatively large number of Ga atoms. FIG. 36(C) shows that a left portion of the area surrounded by the dashed line is relatively dark and a right portion thereof is relatively bright. Thus, it was found that the area surrounded by the dashed line was a region including GaO_(X3), Ga_(X4)Zn_(Y4)O_(Z4), or the like as a main component.

Similarly, areas surrounded by solid lines and dashed lines in the EDX mapping images in FIG. 36(D), FIG. 36(E), and FIG. 36(F) are focused on.

As shown in FIG. 36(D), a relatively bright region occupies a large area in the area surrounded by the solid line and a relatively dark region occupies a large area in the area surrounded by the dashed line. As shown in FIG. 36(E), a relatively dark region occupies a large area in the area surrounded by the solid line and a relatively bright region occupies a large area in the area surrounded by the dashed line.

That is, it was found that the areas surrounded by the solid lines were regions including a relatively large number of In atoms and a relatively small number of Ga atoms. FIG. 36(F) shows that a lower portion of the area surrounded by the solid line is relatively dark and an upper portion thereof is relatively bright. Thus, it was found that the area surrounded by the solid line was a region including In_(X2)Zn_(Y2)O_(Z2), InO_(X1), or the like as a main component.

It was also found that the area surrounded by the dashed line was a region including a relatively small number of In atoms and a region including a relatively large number of Ga atoms. FIG. 36(F) shows that a right portion of the area surrounded by the dashed line is relatively dark and a left portion thereof is relatively bright. Thus, it was found that the area surrounded by the dashed line was a region including GaO_(X3), Ga_(X4)Zn_(Y4)O_(Z4), or the like as a main component.

Furthermore, as shown in FIG. 36 , the In atoms are relatively more uniformly distributed than the Ga atoms, and regions including InO_(X1) as a main component are seemingly joined to each other through a region including In_(X2)Zn_(Y2)O_(Z2) as a main component. It can be thus presumed that the regions including In_(X2)Zn_(Y2)O_(Z2) or InO_(X1) as a main component extend like a cloud.

An In—Ga—Zn oxide having a composition in which the regions including GaO_(X3) as a main component and the regions including In_(X2)Zn_(Y2)O_(Z2) or InO_(X1) as a main component are unevenly distributed and mixed can be referred to as CAC-IGZO.

In FIG. 36 , each of the regions including GaO_(X3) as a main component and the regions including In_(X2)Zn_(Y2)O_(Z2) or InO_(X1) as a main component was observed to have a size greater than or equal to 0.5 nm and less than or equal to 10 nm, or greater than or equal to 1 nm and less than or equal to 3 nm.

As described above, it was confirmed that the CAC-IGZO has a structure different from that of an IGZO compound in which metal elements are evenly distributed, and has characteristics different from those of the IGZO compound. That is, it was confirmed that in the CAC-IGZO, regions including GaO_(X3) or the like as a main component and regions including In_(X2)Zn_(Y2)O_(Z2) or InO_(X1) as a main component were separated to form a mosaic pattern.

Accordingly, it can be expected that when CAC-IGZO is used for a semiconductor element, the property derived from GaO_(X3) or the like and the property derived from In_(X2)Zn_(Y2)O_(Z2) or InO_(X1) complement each other, whereby high on-state current (I_(on)), high field-effect mobility (μ), and low off-state current (I_(off)) can be achieved. A semiconductor element including CAC-IGZO has high reliability. Thus, CAC-IGZO is suitably used in a variety of semiconductor devices typified by a display.

At least part of this example can be implemented in combination with any of the embodiments and the other examples described in this specification as appropriate.

Example 2

In this example, the transistor 150 including the metal oxide 108 of one embodiment of the present invention was fabricated and subjected to tests for electrical characteristics and reliability. In this example, nine transistors, i.e., Sample 2A, Sample 2B, Sample 2C, Sample 2D, Sample 2E, Sample 2F, Sample 2G, Sample 2H, and Sample 2J, were fabricated as the transistor 150 including the metal oxide 108.

<Structure of Samples and Fabrication Method Thereof

Sample 2A, Sample 2B, Sample 2C, Sample 2D, Sample 2E, Sample 2F, Sample 2G, Sample 2H, and Sample 2J relating to one embodiment of the present invention will be described below. As Sample 2A to Sample 2J, the transistors 150 having the structure illustrated in FIG. 7 were fabricated by the fabrication method described in Embodiment 2 with reference to FIG. 9 to FIG. 11 .

Sample 2A to Sample 2J were fabricated at different temperatures and different oxygen flow rate ratios in film formation of the metal oxide 108. The temperatures and the oxygen flow rate ratios in film formation of the metal oxides of Sample 2A to Sample 2J are shown in the following table.

TABLE 3 Formation condition of metal oxide 108 O₂ Formation Flow rate [sccm] ratio temperature O₂ Ar [%] [° C.] Sample 2A 30 270 10 R.T. Sample 2B 90 210 30 R.T. Sample 2C 300 0 100 R.T. Sample 2D 30 270 10 130 Sample 2E 90 210 30 130 Sample 2F 300 0 100 130 Sample 2G 30 270 10 170 Sample 2H 90 210 30 170 Sample 2J 300 0 100 170

The samples were fabricated by the fabrication method described in Embodiment 2. The metal oxide 108 was formed using a metal oxide target (In:Ga:Zn=4:2:4.1 [atomic ratio]).

The transistor 150 had a channel length of 2 μm and a channel width of 3 μm (hereinafter, also referred to as L/W=2/3 μm) or a channel length of 2 μm and a channel width of 50 μm (hereinafter, also referred to as L/W=2/50 μm).

<Electrical Characteristics of Transistors>

Next, I_(d)-V_(g) characteristics of the transistors (L/W=2/3 μm) in Sample 2A to Sample 2J fabricated above were measured. As conditions for measuring the I_(d)-V_(g) characteristics of each transistor, a voltage applied to the conductive film 112 serving as a first gate electrode (hereinafter, the voltage is also referred to as gate voltage (V_(g))) and a voltage applied to the conductive film 106 serving as a second gate electrode (hereinafter, the voltage is also referred to as back gate voltage (V_(bg))) were changed from −10 V to +10 V in increments of 0.25 V. A voltage applied to the conductive film 120 a serving as a source electrode (the voltage is also referred to as source voltage (V_(s))) was 0 V (comm), and a voltage applied to the conductive film 120 b serving as a drain electrode (the voltage is also referred to as drain voltage (V_(d))) was 0.1 V and 20 V.

[I_(d)-V_(g) Characteristics of Transistor]

Here, drain current-gate voltage characteristics (I_(d)-V_(g) characteristics) of a transistor are described. FIG. 39(A) illustrates an example of I_(d)-V_(g) characteristics of the transistor. FIG. 39(A) shows the case where polycrystalline silicon is used for an active layer of the transistor for easy understanding. In FIG. 39(A), the vertical axis and the horizontal axis represent I_(d) (Drain Current) and V_(g) (Gate Voltage), respectively.

As shown in FIG. 39(A), I_(d)-V_(g) characteristics are broadly divided into three regions. A first region, a second region, and a third region are referred to as an off region (OFF region), a subthreshold region, and an on region (ON region), respectively. A gate voltage at a boundary between the subthreshold region and the on region is referred to as a threshold voltage (V_(th)).

To obtain favorable characteristics of the transistor, it is preferable that the drain current in the off region (also referred to as off-state current or I_(off)) be low and the drain current in the on region (also referred to as on-state current or I_(on)) be high. As an index of the on-state current of the transistor, the field-effect mobility is often used. The details of the field-effect mobility will be described later.

To drive the transistor at a low voltage, the slope of the I_(d)-V_(g) characteristics in the subthreshold region is preferably steep. An index of the degree of change in the I_(d)-V_(g) characteristics in the subthreshold region is referred to as subthreshold swing (SS) or an S value. The S value is represented by the following formula (2).

$\begin{matrix} \left\lbrack {{Formula}2} \right\rbrack &  \\ {{SS} = {\min\left( \frac{\partial V_{g}}{\partial{\log_{10}\left( I_{d} \right)}} \right)}} & (2) \end{matrix}$

The S value is a minimum value of the amount of change in gate voltage which is needed for changing a drain current by an order of magnitude in the subthreshold region. As the S value is smaller, switching operation between on and off states can be performed rapidly.

[I_(d)-V_(d) Characteristics of Transistor]

Next, drain current-drain voltage characteristics (I_(d)-V_(d) characteristics) of a transistor are described. FIG. 39(B) shows an example of I_(d)-V_(d) characteristics of the transistor. In FIG. 39(B), the vertical axis and the horizontal axis represent I_(d) and V_(d), respectively.

As illustrated in FIG. 39(B), the on region is further divided into two regions. A first region and a second region are referred to as a linear region and a saturation region, respectively. In the linear region, drain current increases in a parabola shape in accordance with the increase in drain voltage. On the other hand, in the saturation region, drain current does not greatly change even when drain voltage changes. According to a vacuum tube, the linear region and the saturation region are referred to as a triode region and a pentode region, respectively, in some cases.

The linear region indicates the state where V_(g) is higher than V_(d) (V_(d)<V_(g)) in some cases. The saturation region indicates the state where V_(d) is higher than V_(g) (V_(g)<V_(d)) in some cases. However, in practice, the threshold voltage of the transistor needs to be considered. Thus, the state where a value obtained by subtracting the threshold voltage of the transistor from V_(g) is higher than V_(d) (V_(d)<V_(g)−V_(th)) is referred to as the linear region in some cases. Similarly, the state where a value obtained by subtracting the threshold voltage of the transistor from V_(g) is lower than V_(d) (V_(g)−V_(th)<V_(d)) is referred to as the saturation region in some cases.

The I_(d)-V_(a) characteristics of the transistor with which current in the saturation region is constant are expressed as “favorable saturation” in some cases. The favorable saturation of the transistor is important particularly when the transistor is used in an organic EL display. For example, the use of a transistor with favorable saturation as a transistor of a pixel of an organic EL display can suppress a change in luminance of the pixel even when the drain voltage is changed.

[Analysis Model of Drain Current]

Next, an analysis model of the drain current is described. As the analysis model of the drain current, analytic formulae of drain current based on gradual channel approximation (GCA) is known. On the basis of GCA, the drain current of the transistor is represented by the following formula (3).

$\begin{matrix} \left\lbrack {{Formula}3} \right\rbrack &  \\ {I_{d} = \left\{ \begin{matrix} {\mu\frac{W}{L}{C_{OX}\left\lbrack {{\left( {{Vg} - V_{th}} \right)V_{d}} - {\frac{1}{2}V_{d}^{2}}} \right\rbrack}\ldots\left( {{V_{g} - V_{th}} > V_{d}} \right)} \\ {\mu\frac{W}{2L}{C_{OX}\left( {{Vg} - V_{th}} \right)}^{2}\ldots\ \left( {{V_{g} - V_{th}} \leq V_{d}} \right)} \end{matrix} \right.} & (3) \end{matrix}$

In the formula (3), the upper formula is a formula for drain current in a linear region and the lower formula is a formula for drain current in a saturation region. In the formula (3), I_(d) represents the drain current, μ represents the mobility of the active layer, L represents the channel length of the transistor, W represents the channel width of the transistor, Cox represents the gate capacitance, V_(g) represents the gate voltage, V_(d) represents the drain voltage, and V_(th) represents the threshold voltage of the transistor.

[Field-Effect Mobility]

Next, field-effect mobility is described. As an index of current drive capability of a transistor, the field-effect mobility is used. As described above, the on region of the transistor is divided into the linear region and the saturation region. From the characteristics in the regions, the field-effect mobility of the transistor can be calculated on the basis of the analytic formulae of the drain current based on GCA. The field-effect mobility in the linear region and the field-effect mobility in the saturation region are referred to as linear mobility and saturation mobility, respectively, when they need to be distinguished from each other. The linear mobility is represented by the following formula (4) and the saturation mobility is represented by the following formula (5).

$\begin{matrix} \left\lbrack {{Formula}4} \right\rbrack &  \\ {\mu_{FE}^{lin} = {\frac{L}{WC_{OX}}\frac{\partial I_{d}}{\partial V_{g}}\frac{1}{V_{d}}}} & (4) \end{matrix}$ $\begin{matrix} \left\lbrack {{Formula}5} \right\rbrack &  \\ {\mu_{FE}^{sat} = {\frac{2L}{WC_{OX}}\left( \frac{\partial\sqrt{I_{d}}}{\partial V_{g}} \right)^{2}}} & (5) \end{matrix}$

In this specification and the like, curves calculated from the formula (4) and the formula (5) are referred to as mobility curves. FIG. 40 shows mobility curves calculated from the analytic formulae of drain current based on GCA. In FIG. 40 , the I_(d)-V_(g) characteristics at V_(d)=10 V and the mobility curves of the linear mobility and the saturation mobility at the time when GCA is assumed to be effective are shown together (the value of mobility corresponds to the Field-effective mobility on the right vertical axis).

In FIG. 40 , the I_(d)-V_(g) characteristics are calculated from the analytic formulae of drain current based on GCA. The shapes of the mobility curves can be a lead to understanding the state of the inside of the transistor.

FIG. 37 shows the results of I_(d)-V_(g) characteristics and field-effect mobilities of Sample 2A to Sample 2J. The solid line and the dashed-dotted line represent I_(d) at V_(d)=20 V and I_(d) at V_(d)=0.1 V, respectively. The dashed line represents field-effect mobility. In FIG. 37 , the first vertical axis represents I_(d) [A], the second vertical axis represents field-effect mobility (μFE) [cm²/Vs], and the horizontal axis represents V_(g) [V]. The field-effect mobility was calculated from the value measured at V_(g)=20 V.

As shown in FIG. 37 , it was found that Sample 2A to Sample 2J have different on-state currents (I_(on)) and different field-effect mobilities, particularly different field-effect mobilities in saturation regions. In particular, the maximum saturation mobilities and the rising characteristics of the field-effect mobilities around 0 V were found to differ distinctly.

It was found from FIG. 37 that as the substrate temperature at the time of film formation is lower or the oxygen flow rate ratio at the time of film formation is lower, the on-state current (I_(on)) becomes higher. It was also found that the field-effect mobility rises more steeply around 0 V. In particular, Sample 2A was found to have a maximum field-effect mobility close to 70 cm²/Vs.

<Gate Bias-Temperature Stress Test (GBT Test)>

Next, the reliability of the above transistors (L/W=2/50 μm) of Sample 2A to Sample 2J was evaluated. As the reliability evaluation, GBT tests were used.

The conditions for GBT tests in this example were as follows. A voltage applied to the conductive film 112 serving as the first gate electrode and the conductive film 106 serving as the second gate electrode (hereinafter referred to as gate voltage (V_(g))) was ±30 V, and a voltage applied to a conductive film functioning as the conductive film 120 a serving as the source electrode and the conductive film 120 b serving as a drain electrode (hereinafter referred to as source voltage (V_(s)) and drain voltage (V_(d)), respectively) was 0 V (COMMON). The stress temperature was 60° C., the time for stress application was 1 hour, and two kinds of measurement environments, a dark environment and a photo environment (irradiation with light at approximately 10,000 lx from a white LED), were employed.

In other words, the conductive film 120 a serving as the source electrode of the transistor 150 and the conductive film 120 b serving as the drain electrode of the transistor 150 were set at the same potential, and a potential different from that of the conductive film 120 a serving as the source electrode and the conductive film 120 b serving as the drain electrode was applied to the conductive film 112 serving as the first gate electrode and the conductive film 106 serving as the second gate electrode for a certain time (here, one hour).

A case where the potential applied to the conductive film 112 serving as the first gate electrode and the conductive film 106 serving as the second gate electrode is higher than the potential applied to the conductive film 120 a serving as the source electrode and the conductive film 120 b serving as the drain electrode is called positive stress. A case where the potential applied to the conductive film 112 serving as the first gate electrode and the conductive film 106 serving as the second gate electrode is lower than the potential applied to the conductive film 120 a serving as the source electrode and the conductive film 120 b serving as the drain electrode is called negative stress. Thus, the reliability evaluation was performed under four conditions in total, i.e., positive GBT (dark), negative GBT (dark), positive GBT (light irradiation), and negative GBT (light irradiation).

Note that in the following description, the positive GBT (dark) is referred to as positive bias temperature stress (PBTS). The negative GBT (dark) is referred to as negative bias temperature stress (NBTS). The positive GBT (light irradiation) is referred to as positive bias illumination temperature stress (PBITS). The negative GBT (light irradiation) is referred to as negative bias illumination temperature stress (NBITS).

FIG. 38 shows the GBT test results of Sample 2A to Sample 2J. In FIG. 38 , the vertical axis represents the amount of shift in the threshold voltage (ΔV_(th)) of the transistors.

The results in FIG. 38 indicate that the amount of shift in the threshold voltage (ΔV_(th)) of each of the transistors included in Sample 2A to Sample 2J was within ±3 V in the GBT tests. Thus, it is confirmed that the transistors included in Sample 2A to Sample 2J each have high reliability.

Thus, even the IGZO film having low crystallinity is presumed to have a low density of defect states like an IGZO film having high crystallinity.

At least part of this example can be implemented in combination with any of the embodiments and the other examples described in this specification as appropriate.

Example 3

In this example, a metal oxide of one embodiment of the present invention, which was formed over a substrate, was measured with a variety of methods, and the measurement results are described. Note that in this example, Sample 3A, Sample 3D, and Sample 3J were fabricated.

<Structure of Samples and Fabrication Method Thereof>

Sample 3A, Sample 3D, and Sample 3J relating to one embodiment of the present invention are described below. Sample 3A, Sample 3D, and Sample 3J each include a substrate and a metal oxide over the substrate.

Sample 3A, Sample 3D, and Sample 3J were fabricated at different temperatures and different oxygen flow rate ratios in film formation of the metal oxide. The temperatures and the oxygen flow rate ratios in film formation of the metal oxides of Sample 3A, Sample 3D, and Sample 3J are shown in the following table.

TABLE 4 O₂ Formation Flow rate [sccm] ratio temperature O₂ Ar [%] [° C.] Sample 3A 30 270 10 R.T. Sample 3D 30 270 10 130 Sample 3J 150 150 50 170

Next, methods for fabricating the samples will be described.

A glass substrate was used as the substrate. Over the substrate, a 100-nm-thick In—Ga—Zn metal oxide was formed as a metal oxide with a sputtering apparatus. The formation conditions were as follows: the pressure in a chamber was 0.6 Pa; and a metal oxide target (an atomic ratio of In:Ga:Zn=1:1:1.2) was used as a target. The metal oxide target provided in the sputtering apparatus was supplied with an AC power of 2500 W, so that the metal oxide film was formed.

The formation temperatures and oxygen flow rate ratios shown in the above table were used as the conditions for forming metal oxide films to fabricate Sample 3A, Sample 3D, and Sample 3J.

Through the above steps, Sample 3A, Sample 3D, and Sample 3J in this example were fabricated.

<TEM Images and Electron Diffraction>

This section describes the TEM observation and analysis results of Sample 3A, Sample 3D, and Sample 3J.

This section also describes electron diffraction patterns obtained by irradiation of Sample 3A, Sample 3D, and Sample 3J with an electron beam with a probe diameter of 1 nm (also referred to as a nanobeam electron beam).

The plan-view TEM images were observed with a spherical aberration corrector function. The HAADF-STEM images were obtained using an atomic resolution analytical electron microscope JEM-ARM200F manufactured by JEOL Ltd. under the following conditions: the acceleration voltage was 200 kV; and irradiation with an electron beam with a diameter of approximately 0.1 nmφ was performed.

Note that the electron diffraction patterns were observed while an electron beam irradiation was performed at a constant rate from 0 second to 35 seconds.

FIG. 41(A) shows a cross-sectional TEM image of Sample 3A, and FIG. 41(B) shows an electron diffraction pattern of Sample 3A. FIG. 41(C) shows a cross-sectional TEM image of Sample 3D, and FIG. 41(D) shows an electron diffraction pattern of Sample 3D. FIG. 41(E) shows a cross-sectional TEM image of Sample 3J, and FIG. 41(F) shows an electron diffraction pattern of Sample 3J.

A nanocrystal was found in Sample 3A from the result of the cross-sectional TEM observation as shown in FIG. 41(A). As shown in FIG. 41(B), the observed electron diffraction pattern of Sample 3A has a region with high luminance in a circular (ring) pattern. Furthermore, a plurality of spots were observed in the ring-shaped region.

Sample 3D was found to have a CAAC structure and a nanocrystal from the result of the cross-sectional TEM observation shown in FIG. 41(C). As shown in FIG. 41(D), the observed electron diffraction pattern of Sample 3D has a region with high luminance in a circular (ring) pattern. Furthermore, a plurality of spots were observed in the ring-shaped region. In the diffraction pattern, spots derived from the (009) plane were slightly observed.

Meanwhile, Sample 3J was clearly found to have layered arrangement of a CAAC structure from the result of the cross-sectional TEM observation in FIG. 41(E). Furthermore, spots derived from the (009) plane were found in the result of the electron diffraction pattern of Sample 3J shown in FIG. 41(F).

The features observed in the cross-sectional TEM images and the plan-view TEM images are one aspect of a structure of a metal oxide.

As described above, the electron diffraction patterns of Sample 3A and Sample 3D each have a region with high luminance in a ring pattern and a plurality of bright spots appear in the ring-shaped region. It was thus found that Sample 3A and Sample 3D exhibit an electron diffraction pattern of the metal oxide including nanocrystals and do not show alignment in the plane direction and the cross-sectional direction. Sample 3D was found to be a mixed material of the nc structure and the CAAC structure.

Meanwhile, the electron diffraction pattern of Sample 3J includes spots derived from the (009) plane of an InGaZnO₄ crystal. It was thus found that Sample 3J had c-axis alignment and the c-axes were aligned in the direction substantially perpendicular to the formation surface or the top surface of Sample 3J.

<Analysis of TEM Image>

This section describes the observation and analysis results of Sample 3A, Sample 3D, and Sample 3J with an HAADF-STEM.

The results of image analysis of plan-view TEM images are described. The plan-view TEM images were obtained with a spherical aberration corrector function. The plan-view TEM images were obtained using an atomic resolution analytical electron microscope JEM-ARM200F manufactured by JEOL Ltd. under the following conditions: the acceleration voltage was 200 kV; and irradiation with an electron beam with a diameter of approximately 0.1 nmφ was performed.

FIG. 42(A) shows a plan-view TEM image of Sample 3A, and FIG. 42(B) shows an image obtained through image processing of the plan-view TEM image of Sample 3A. FIG. 42(C) shows a plan-view TEM image of Sample 3D and FIG. 42(D) shows an image obtained through image processing of the plan-view TEM image of Sample 3D. FIG. 42(E) shows a plan-view TEM image of Sample 3J and FIG. 42(F) shows an image obtained through image processing of the plan-view TEM image of Sample 3J.

The images obtained through image processing was then shown in such a manner that color or gradation changes in accordance with the angle of the hexagonal lattice in the region. The images obtained through image processing of the plan-view TEM images in FIG. 42(B), FIG. 42(D), and FIG. 42(F) are images obtained by performing image analysis on the plan-view TEM images in FIG. 42(A), FIG. 42(C), and FIG. 42(E) by the method described in Example 1 and applying gradation in accordance with the angle of the hexagonal lattice. In other words, the images obtained through the image processing of the plan-view TEM images are images in which the orientations of lattice points in certain wavenumber ranges are extracted by color-coding the certain wavenumber ranges in an FFT filtering image of the plan-view TEM image.

As shown in FIG. 42 , in Sample 3A and Sample 3D in which nc was observed, the hexagons were oriented randomly and distributed in a mosaic pattern. In Sample 3J in which a layered structure was observed in the cross-sectional TEM image, regions with uniformly oriented hexagons exist in a large area of several tens of nanometers. It was found that Sample 3D included an nc region in a random mosaic pattern and a large-area region with uniform orientation as in Sample 3J.

It was found from FIG. 42 that as the substrate temperature at the time of film formation is lower or the oxygen gas flow rate ratio at the time of film formation is lower, regions in which the hexagons are oriented randomly and distributed in a mosaic pattern are likely to exist.

Through the analysis of a plan-view TEM image of a CAAC-OS, a boundary portion where angles of hexagonal lattices change can be examined.

Next, Voronoi diagrams were formed using lattice point groups in Sample 3A. The Voronoi diagrams were obtained by the method described in Example 1.

FIG. 43(A), FIG. 43(B), and FIG. 43(C) show the proportions of the shapes of Voronoi regions (any of tetragon to enneagon) in Sample 3A, Sample 3D, and Sample 3J, respectively. Bar graphs show the numbers of the shapes of Voronoi regions (any of tetragon to enneagon) in the samples. Furthermore, tables show the proportions of the shapes of Voronoi regions (any of tetragon to enneagon) in the samples.

It was found from FIG. 43 that the proportion of hexagons was likely to be high in Sample 3J with a high degree of crystallinity and the proportion of hexagons was likely to be low in Sample 3A with a low degree of crystallinity. The proportion of hexagons in Sample 3D was between that in Sample 3J and that of Sample 3A. Accordingly, it was found from FIG. 43 that the crystal state of the metal oxide significantly differs under different formation conditions.

It was found from FIG. 43 that as the substrate temperature at the time of film formation is lower or the oxygen gas flow rate ratio at the time of film formation is lower, the degree of crystallinity is lower and the proportion of hexagons is lower.

<Elementary Analysis>

This section describes the analysis results of elements included in Sample 3A. For the analysis, by energy dispersive X-ray spectroscopy (EDX), EDX mapping images are obtained and evaluated. An energy dispersive X-ray spectrometer Analysis Station JED-2300T manufactured by JEOL Ltd. is used as an elementary analysis apparatus in the EDX measurement. A Si drift detector is used to detect an X-ray emitted from the sample.

In the EDX measurement, an EDX spectrum of a point is obtained in such a manner that electron beam irradiation is performed on the point in a detection target region of a sample, and the energy of characteristic X-ray of the sample generated by the irradiation and its frequency are measured. In this example, peaks of an EDX spectrum of the point are attributed to electron transition to the L shell in an In atom, electron transition to the K shell in a Ga atom, and electron transition to the K shell in a Zn atom and the K shell in an O atom, and the proportions of the atoms in the point are calculated. An EDX mapping image indicating distributions of proportions of atoms can be obtained through the process in an analysis target region of a sample.

FIG. 44 shows a cross-sectional TEM image, a plan-view TEM image, and EDX mapping images of Sample 3A. In the EDX mapping images, the proportion of an element is indicated by grayscale: the more measured elements exist in a region, the brighter the region is; the less measured elements exist in a region, the darker the region is. The magnification of the EDX mapping images in FIG. 44 is 7,200,000 times.

FIG. 44(A) shows a cross-sectional TEM image, and FIG. 44(E) shows a plan-view TEM image. FIG. 44(B) shows a cross-sectional EDX mapping image of In atoms, and FIG. 44(F) shows a plan-view EDX mapping image of In atoms. In the EDX mapping image in FIG. 44(B), the proportion of the In atoms in all the atoms is the range of 8.64 to 34.91 [atomic %]. In the EDX mapping image in FIG. 44(F), the proportion of the In atoms in all the atoms is in the range of 5.76 to 34.69 [atomic %].

FIG. 44(C) shows a cross-sectional EDX mapping image of Ga atoms, and FIG. 44(G) shows a plan-view EDX mapping image of Ga atoms. In the EDX mapping image in FIG. 44(C), the proportion of the Ga atoms in all the atoms is in the range of 2.45 to 25.22 [atomic %]. In the EDX mapping image in FIG. 44(G), the proportion of the Ga atoms in all the atoms is in the range of 1.29 to 27.64 [atomic %].

FIG. 44(D) shows a cross-sectional EDX mapping image of Zn atoms, and FIG. 44(H) shows a plan-view EDX mapping image of Zn atoms. In the EDX mapping image in FIG. 44(D), the proportion of the Zn atoms in all the atoms is in the range of 5.05 to 23.47 [atomic %]. In the EDX mapping image in FIG. 44(H), the proportion of the Zn atoms in all the atoms is in the range of 3.69 to 27.86 [atomic %].

Note that FIG. 44(A), FIG. 44(B), FIG. 44(C), and FIG. 44(D) show the same region in the cross section of Sample 3A. FIG. 44(E), FIG. 44(F), FIG. 44(G), and FIG. 44(H) show the same region in the plane of Sample 3A.

FIG. 45 shows enlarged cross-sectional EDX mapping images of Sample 3A. FIG. 45(A) is an enlarged view of a part in FIG. 44(B). FIG. 45(B) is an enlarged view of a part in FIG. 44(C). FIG. 45(C) is an enlarged view of a part in FIG. 44(D).

The EDX mapping images in FIG. 45(A), FIG. 45(B), and FIG. 45(C) show relative distribution of bright and dark areas, indicating that the atoms have distributions in Sample 3A. Areas surrounded by solid lines and areas surrounded by dashed lines in FIG. 45(A), FIG. 45(B), and FIG. 45(C) were focused on.

As shown in FIG. 45(A), a relatively dark region occupies a large area in the area surrounded by the solid line and a relatively bright region occupies a large area in the area surrounded by the dashed line. As shown in FIG. 45(B), a relatively bright region occupies a large area in the area surrounded by the solid line and a relatively dark region occupies a large area in the area surrounded by the dashed line.

That is, it was found that the areas surrounded by the solid lines were regions including a relatively large number of In atoms and the areas surrounded by the dashed lines were regions including a relatively small number of In atoms. FIG. 45(C) shows that an upper portion of the area surrounded by the solid line is relatively bright and a lower portion thereof is relatively dark. Thus, it was found that the area surrounded by the solid line was a region including In_(X2)Zn_(Y2)O_(Z2), InO_(X1), or the like as a main component.

It was also found that the area surrounded by the solid line was a region including a relatively small number of Ga atoms and the area surrounded by the dashed line was a region including a relatively large number of Ga atoms. FIG. 45(C) shows that a right portion of the area surrounded by the upper dashed line is relatively bright and a left portion thereof is relatively dark. FIG. 45(C) also shows that an upper left portion of the area surrounded by the lower dashed line is relatively bright and a lower right portion thereof is relatively dark. Thus, it was found that the area surrounded by the dashed line was a region including GaO_(X3), Ga_(X4)Zn_(Y4)O_(Z4), or the like as a main component.

Furthermore, as shown in FIG. 45(A), FIG. 45(B), and FIG. 45(C), the In atoms are relatively more uniformly distributed than the Ga atoms, and regions including InO_(X1) as a main component are seemingly joined to each other through a region including In_(X2)Zn_(Y2)O_(Z2) as a main component. It can be thus presumed that the regions including In_(X2)Zn_(Y2)O_(Z2) or InO_(X1) as a main component extend like a cloud.

An In—Ga—Zn oxide having a composition in which the regions including GaO_(X3) as a main component and the regions including In_(X2)Zn_(Y2)O_(Z2) or InO_(X1) as a main component are unevenly distributed and mixed can be referred to as CAC-IGZO.

In FIG. 45(A), FIG. 45(B), and FIG. 45(C), each of the regions including GaO_(X3) as a main component and the regions including In_(X2)Zn_(Y2)O_(Z2) or InO_(X1) as a main component was observed to have a size greater than or equal to 0.5 nm and less than or equal to 10 nm, or greater than or equal to 1 nm and less than or equal to 3 nm.

FIG. 46 shows a cross-sectional TEM image, a plan-view TEM image, and EDX mapping images of Sample 3J. In the EDX mapping images, the proportion of an element is indicated by grayscale: the more measured elements exist in a region, the brighter the region is; the less measured elements exist in a region, the darker the region is. The magnification of the EDX mapping images in FIG. 46 is 7,200,000 times.

FIG. 46(A) shows a cross-sectional TEM image, and FIG. 46(E) shows a plan-view TEM image. FIG. 46(B) shows a cross-sectional EDX mapping image of In atoms, and FIG. 46(F) shows a plan-view EDX mapping image of In atoms. In the EDX mapping image in FIG. 46(B), the proportion of the In atoms in all the atoms is the range of 9.70 to 40.47 [atomic %]. In the EDX mapping image in FIG. 46(F), the proportion of the In atoms in all the atoms is in the range of 9.16 to 35.76 [atomic %].

FIG. 46(C) shows a cross-sectional EDX mapping image of Ga atoms, and FIG. 46(G) shows a plan-view EDX mapping image of Ga atoms. In the EDX mapping image in FIG. 46(C), the proportion of the Ga atoms in all the atoms is in the range of 8.23 to 31.95 [atomic %]. In the EDX mapping image in FIG. 46(G), the proportion of the Ga atoms in all the atoms is in the range of 8.21 to 28.86 [atomic %].

FIG. 46(D) shows a cross-sectional EDX mapping image of Zn atoms, and FIG. 46(H) shows a plan-view EDX mapping image of Zn atoms. In the EDX mapping image in FIG. 46(D), the proportion of the Zn atoms in all the atoms is in the range of 5.37 to 25.92 [atomic %]. In the EDX mapping image in FIG. 46(H), the proportion of the Zn atoms in all the atoms is in the range of 7.86 to 24.36 [atomic %].

Note that FIG. 46(A), FIG. 46(B), FIG. 46(C), and FIG. 46(D) show the same region in the cross section of Sample 3J. FIG. 46(E), FIG. 46(F), FIG. 46(G), and FIG. 46(H) show the same region in the plane of Sample 3J.

In FIG. 46(A), a group of laterally grown crystals is clearly observed, and in FIG. 46(E), crystals having a hexagonal structure with an angle of 120° are observed.

The EDX mapping images of the In atoms and the Zn atoms in FIG. 46(B) and FIG. 46(D) show particularly bright spots aligned as indicated by white lines. In FIG. 46(F) and FIG. 46(H), these lines form an angle of approximately 120°, which is characteristic of the hexagonal structure, and in FIG. 46(B) and FIG. 46(D), the same layered arrangement as in FIG. 46(A) can be observed. As shown in FIG. 46(C) and FIG. 46(G), such a tendency is not observed for Ga atoms.

The resolution of EDX is generally affected by the regularity of atomic arrangement. When atoms are regularly arranged as in a single crystal, the atoms are arranged linearly in the beam incident direction, and incident electrons are therefore channeled and propagated along the atom rows. Thus, atomic columns can be separated. In contrast, when the regularity of atomic arrangement is low, the atom rows are out of alignment and incident electrons are therefore scattered without being channeled. That is, the spatial resolution is low and an obtained image is in a blurred state in some cases.

That is, since the crystallinity of CAAC is not as high as that of single crystal, a beam is broadened and the resolution of EDX mapping is not as high as that of HAADF-STEM; thus, CAAC is probably observed in a blurred state. From FIG. 44 , CAC is blurred because of a broadened beam; thus, the atoms are determined to be nanoparticles with a blurry boundary.

As described above, it is confirmed that the CAC-IGZO has a structure different from that of an IGZO compound in which metal elements are evenly distributed, and has characteristics different from those of the IGZO compound. That is, it was confirmed that in the CAC-IGZO, regions including GaO_(X3) or the like as a main component and regions including In_(X2)Zn_(Y2)O_(Z2) or InO_(X1) as a main component were separated to form a mosaic pattern.

Accordingly, it can be expected that when CAC-IGZO is used for a semiconductor element, the property derived from GaO_(X3) or the like and the property derived from In_(X2)Zn_(Y2)O_(Z2) or InO_(X1) complement each other, whereby high on-state current (I_(on)), high field-effect mobility (μ), and low off-state current (I_(off)) can be achieved. A semiconductor element including CAC-IGZO has high reliability. Thus, CAC-IGZO is suitably used in a variety of semiconductor devices typified by a display.

At least part of this example can be implemented in combination with any of the embodiments and the other examples described in this specification as appropriate.

Example 4

In this example, the transistor 150 including the metal oxide 108 of one embodiment of the present invention was fabricated and subjected to tests for electrical characteristics and reliability. In this example, nine transistors, i.e., Sample 4A, Sample 4B, Sample 4C, Sample 4D, Sample 4E, Sample 4F, Sample 4G, Sample 4H, and Sample 4J, were fabricated as the transistor 150 including the metal oxide 108.

<Structure of Samples and Fabrication Method Thereof>

Sample 4A, Sample 4B, Sample 4C, Sample 4D, Sample 4E, Sample 4F, Sample 4G, Sample 4H, and Sample 4J relating to one embodiment of the present invention will be described below. As Sample 4A to Sample 4J, the transistors 150 having the structure illustrated in FIG. 7 were fabricated by the fabrication method described in Embodiment 2 with reference to FIG. 9 to FIG. 11 .

Sample 4A to Sample 4J were fabricated at different temperatures and different oxygen flow rate ratios in film formation of the metal oxide 108. The temperatures and the oxygen flow rate ratios in film formation of the metal oxides of Sample 4A to Sample 4J are shown in the following table.

TABLE 5 Formation condition of metal oxide 108 O₂ Formation Flow rate [sccm] ratio temperature O₂ Ar [%] [° C.] Sample 4A 30 270 10 R.T. Sample 4B 90 210 30 R.T. Sample 4C 150 150 50 R.T. Sample 4D 30 270 10 130 Sample 4E 90 210 30 130 Sample 4F 150 150 50 130 Sample 4G 30 270 10 170 Sample 4H 90 210 30 170 Sample 4J 150 150 50 170

The samples were fabricated by the fabrication method described in Embodiment 2. The metal oxide 108 was formed using a metal oxide target (In:Ga:Zn=1:1:1.2 [atomic ratio]).

The transistor 150 had a channel length of 2 μm and a channel width of 3 μm (hereinafter, also referred to as L/W=2/3 μm).

<I_(d)-V_(g) Characteristics of Transistor>

Next, I_(d)-V_(g) characteristics of the transistors (L/W=2/3 μm) in Sample 4A to Sample 4J fabricated above were measured. As conditions for measuring the I_(d)-V_(g) characteristics of each transistor, a voltage applied to the conductive film 112 serving as a first gate electrode (hereinafter, the voltage is also referred to as gate voltage (V_(g))) and a voltage applied to the conductive film 106 serving as a second gate electrode (hereinafter, the voltage is also referred to as back gate voltage (V_(bg))) were changed from −10 V to +10 V in increments of 0.25 V. A voltage applied to the conductive film 120 a serving as a source electrode (the voltage is also referred to as source voltage (V_(s))) was 0 V (comm), and a voltage applied to the conductive film 120 b serving as a drain electrode (the voltage is also referred to as drain voltage (V_(d))) was 0.1 V and 20 V.

FIG. 47 shows the results of I_(d)-V_(g) characteristics and field-effect mobilities of Sample 4A to Sample 4J. The solid line and the dashed-dotted line represent I_(d) at V_(d)=20 V and I_(d) at V_(d)=0.1 V, respectively. The dashed line and the dotted line represent field-effect mobility calculated from a value measured at V_(d)=20 V and field-effect mobility calculated from a value measured at V_(d)=0.1 V, respectively. In FIG. 47 , the first vertical axis represents I_(d) [A], the second vertical axis represents field-effect mobility (μFE) [cm²/Vs], and the horizontal axis represents V_(g) [V].

FIG. 47 shows that the transistors 150 of Sample 4A to Sample 4J have normally-off characteristics. As shown in FIG. 47 , it was found that Sample 4A to Sample 4J have different on-state currents (I_(on)) and different field-effect mobilities, particularly different field-effect mobilities in saturation regions. In particular, the maximum saturation mobilities and the rising characteristics of the field-effect mobilities around 0 V were found to differ distinctly.

It was found from FIG. 47 that as the substrate temperature at the time of film formation is lower or the oxygen flow rate ratio at the time of film formation is lower, the field-effect mobility at low V_(g) is significantly higher. In particular, Sample 4A was found to have a maximum field-effect mobility close to 40 cm²/Vs. The high mobility at low V_(g) is suitable for high-speed driving at low voltage; therefore, application to a variety of semiconductor devices typified by a display can be expected.

From FIG. 47 , different behavior of field-effect mobility was found at V_(d)=20 V (shown by dashed lines) and V_(d)=0.1 V (shown by dotted lines). As V_(g) is increased, the field-effect mobility measured at V_(d)=20 V (shown by dashed lines) becomes higher. This is considered as an influence of heat generation of the transistor. Meanwhile, the field-effect mobility measured at V_(d)=0.1 V (shown by dotted lines) in a high V_(g) range substantially coincides with an ideal saturation mobility curve calculated by the above formula (5).

At least part of this example can be implemented in combination with any of the embodiments and the other examples described in this specification as appropriate.

Example 5

In this example, the analysis results of elements included in a sample will be described. For the analysis, by energy dispersive X-ray spectroscopy (EDX), an EDX mapping image of a metal oxide film of one embodiment of the present invention formed over a substrate is obtained and evaluated. An energy dispersive X-ray spectrometer Analysis Station JED-2300T manufactured by JEOL Ltd. was used as an elementary analysis apparatus in the EDX measurement. A Si drift detector was used to detect an X-ray emitted from the sample.

<Structure of Samples and Fabrication Method Thereof>

In this example, Sample 5A was fabricated. Sample 5A includes a substrate and a metal oxide over the substrate.

Next, a method for fabricating the sample will be described.

A glass substrate was used as the substrate. Over the substrate, a 100-nm-thick In—Ga—Zn metal oxide was formed as a metal oxide with a sputtering apparatus. The formation conditions were as follows: the pressure in a chamber was 0.6 Pa; an atmosphere using an Ar gas at a flow rate of 270 sccm and an O₂ gas at a flow rate of 30 sccm was employed as sputtering gases; and a metal oxide target (In:Ga:Zn=4:2:4.1 [atomic ratio]) was used as a target. The metal oxide target provided in the sputtering apparatus was supplied with an AC power of 2500 W, so that the metal oxide film was formed.

Through the above steps, Sample 5A of this example was fabricated.

<Measurement Results>

In the EDX measurement, an EDX spectrum of a point is obtained in such a manner that electron beam irradiation is performed on the point in a detection target region of a sample, and the energy of characteristic X-ray of the sample generated by the irradiation and its frequency are measured. In this example, peaks of an EDX spectrum of the point are attributed to electron transition to the L shell in an In atom, electron transition to the K shell in a Ga atom, and electron transition to the K shell in a Zn atom and the K shell in an O atom, and the proportions of the atoms in the point are calculated. An EDX mapping image indicating distributions of proportions of atoms can be obtained through the process in an analysis target region of a sample.

FIG. 48 shows measurement results of a cross section of Sample 5A. FIG. 48(A) shows a cross-sectional TEM image, and FIG. 48(B) and FIG. 48(C) show cross-sectional EDX mapping images. In the EDX mapping images, the proportion of an element is indicated by grayscale: the more measured elements exist in a region, the brighter the region is; the less measured elements exist in a region, the darker the region is. The magnification of the EDX mapping images in FIG. 48 is 7,200,000 times. Note that FIG. 48(A), FIG. 48(B), and FIG. 48(C) show the same region in the cross section of Sample 5A.

FIG. 48(B) shows a cross-sectional EDX mapping image of In atoms. In the EDX mapping image in FIG. 48(B), the proportion of the In atoms in all the atoms is the range of 12.11 to 40.30 [atomic %]. FIG. 48(C) shows a cross-sectional EDX mapping image of Ga atoms. In the EDX mapping image in FIG. 48(C), the proportion of the Ga atoms in all the atoms is in the range of 0.00 to 13.18 [atomic %].

The EDX mapping images in FIG. 48(B) and FIG. 48(C) show relative distribution of bright and dark areas, indicating that the In atoms and the Ga atoms have distributions in Sample 5A. Here, five regions surrounded by black lines (a region 901, a region 902, a region 903, a region 904, and a region 905) were extracted among regions whose luminance is greater than or equal to 75% of the maximum luminance in FIG. 48(B). Five regions surrounded by dashed lines (a region 906, a region 907, a region 908, a region 909, and a region 910) were extracted among regions whose luminance is greater than or equal to 75% of the maximum luminance in FIG. 48(C). Five regions surrounded by white lines (a region 911, a region 912, a region 913, a region 914, and a region 915) were extracted among regions whose luminance is greater than or equal to 25% and less than or equal to 75% of the maximum luminance in FIG. 48(B), and among regions whose luminance is greater than or equal to 25% and less than or equal to 75% of the maximum luminance in FIG. 48(C).

In other words, the region 901 to the region 905 are regions including a relatively large number of In atoms. The region 906 to the region 910 are regions including a relatively large number of Ga atoms. The region 911 to the region 915 are regions including an average number of In atoms and Ga atoms.

Regions including a relatively large number of Ga atoms, that is, the five regions surrounded by the dashed lines (the region 906, the region 907, the region 908, the region 909, and the region 910) in FIG. 48(C) were found to be relatively dark in FIG. 48(B). That is, the region including a relatively large number of Ga atoms is expected to include a relatively small number of In atoms.

The proportions of elements in the region 901 to the region 915 in FIG. 48(B) are shown in FIG. 48(D). The regions surrounded by the black lines (the region 901, the region 902, the region 903, the region 904, and the region 905) were found to include a relatively large number of In atoms and a relatively small number of Ga atoms. The regions surrounded by the dashed lines (the region 906, the region 907, the region 908, the region 909, and the region 910) were found to include a relatively small number of In atoms and a relatively large number of Ga atoms.

FIG. 49 shows measurement results of a plane of Sample 5A. FIG. 49(A) shows a plan-view TEM image, and FIG. 49(B) and FIG. 49(C) show plan-view EDX mapping images. Note that FIG. 49(A), FIG. 49(B), and FIG. 49(C) show the same region in the plane of Sample 5A.

FIG. 49(B) shows a plan-view EDX mapping image of In atoms. In the EDX mapping image in FIG. 49(B), the proportion of the In atoms in all the atoms is the range of 12.11 to 43.80 [atomic %]. FIG. 49(C) shows a plan-view EDX mapping image of Ga atoms. In the EDX mapping image in FIG. 49(C), the proportion of the Ga atoms in all the atoms is in the range of 0.00 to 14.83 [atomic %].

The EDX mapping images in FIG. 49(B) and FIG. 49(C) show relative distribution of bright and dark areas, indicating that the In atoms and the Ga atoms have distributions in Sample 5A. Here, five regions surrounded by black lines (a region 921, a region 922, a region 923, a region 924, and a region 925) were extracted among regions whose luminance is greater than or equal to 75% of the maximum luminance in FIG. 49(B). Five regions surrounded by dashed lines (a region 926, a region 927, a region 928, a region 929, and a region 930) were extracted among regions whose luminance is greater than or equal to 75% of the maximum luminance in FIG. 49(C). Five regions surrounded by white lines (a region 931, a region 932, a region 933, a region 934, and a region 935) were extracted among regions whose luminance is greater than or equal to 25% and less than or equal to 75% of the maximum luminance in FIG. 49(B), and among regions whose luminance is greater than or equal to 25% and less than or equal to 75% of the maximum luminance in FIG. 49(C).

Regions including a relatively large number of Ga atoms, that is, the five regions surrounded by the dashed lines (the region 926, the region 927, the region 928, the region 929, and the region 930) in FIG. 49(C) were found to be relatively dark in FIG. 49(B). That is, the region including a relatively large number of Ga atoms is expected to include a relatively small number of In atoms.

The proportions of elements in the region 921 to the region 935 in FIG. 49(B) are shown in FIG. 49(D). The regions surrounded by the black lines (the region 921, the region 922, the region 923, the region 924, and the region 925) were found to include a relatively large number of In atoms and a relatively small number of Ga atoms. The regions surrounded by the dashed lines (the region 926, the region 927, the region 928, the region 929, and the region 930) were found to include a relatively small number of In atoms and a relatively large number of Ga atoms.

As shown in FIG. 48(D) and FIG. 49(D), it was found that the In atoms were distributed in a range of higher than or equal to 25 atomic % and lower than or equal to 60 atomic %. Furthermore, it was found that the Ga atoms were distributed in a range of higher than or equal to 3 atomic % and lower than or equal to 40 atomic %.

A region including a relatively large number of In atoms can be expected to have relatively high conductivity. In contrast, a region including a relatively large number of Ga atoms can be expected to have a relatively high insulating property. Accordingly, it is considered that carriers flow through the region including a relatively large number of In atoms, so that the conductivity property is exhibited and high field-effect mobility (μ) is achieved. Meanwhile, it is considered that distributing the region including a relatively large number of Ga atoms in the metal oxide probably reduces leakage current and achieves favorable switching operation.

In other words, when a metal oxide having a CAC composition is used in a semiconductor element, the insulating property derived from a Ga atom or the like and the conductivity derived from an In atom complement each other, whereby high on-state current (I_(on)) and high field-effect mobility (μ) can be achieved.

At least part of this example can be implemented in combination with any of the embodiments and the other examples described in this specification as appropriate.

Example 6

In this example, the transistor 150 including the metal oxide 108 of one embodiment of the present invention was fabricated and the density of defect states was measured. In this example, nine transistors, i.e., Sample 6A, Sample 6B, Sample 6C, Sample 6D, Sample 6E, Sample 6F, Sample 6G, Sample 6H, and Sample 6J, were fabricated as the transistor 150 including the metal oxide 108.

<Structure of Samples and Fabrication Method Thereof>

Sample 6A to Sample 6J relating to one embodiment of the present invention will be described below. As Sample 6A to Sample 6J, the transistors 150 having the structure illustrated in FIG. 7 were fabricated by the fabrication method described in Embodiment 2 with reference to FIG. 9 to FIG. 11 .

Sample 6A to Sample 6J were fabricated at different temperatures and different oxygen flow rate ratios in film formation of the metal oxide 108. The metal oxide 108 was formed using a metal oxide target (In:Ga:Zn=1:1:1.2 [atomic ratio]). The temperatures and the oxygen flow rate ratios in film formation of the metal oxides of Sample 6A to Sample 6J are shown in the following table.

TABLE 6 O₂ Formation Flow rate [sccm] ratio temperature O₂ Ar [%] [° C.] Sample 6A 30 270 10 R.T. Sample 6B 90 210 30 R.T. Sample 6C 150 150 50 RT. Sample 6D 30 270 10 130 Sample 6E 90 210 30 130 Sample 6F 150 150 50 130 Sample 6G 30 270 10 170 Sample 6H 90 210 30 170 Sample 6J 150 150 50 170

The samples were fabricated by the fabrication method described in Embodiment 2.

The transistor 150 had a channel length of 2 μm and a channel width of 3 (hereinafter, also referred to as L/W=2/3 μm) or a channel length of 2 μm and a channel width of 50 μm (hereinafter, also referred to as L/W=2/50 μm).

<Measurement of Shallow Defect States Using Transistor Characteristics> [Measurement Method of Density of Shallow Defect States]

Shallow defect states (hereinafter, also referred to as sDOS) of a metal oxide can be estimated from electrical characteristics of a transistor in which the metal oxide was used as a semiconductor. In the following description, the density of interface states of the transistor was measured; and a method for estimating subthreshold leakage current in consideration of the density of interface states and the number of electrons trapped by the interface states, N_(trap) is described.

The number of electrons trapped by the interface states, N_(trap), can be measured by, for example, comparing drain current-gate voltage (I_(d)-V_(g)) characteristics of the transistor that were actually measured and drain current-gate voltage (I_(d)-V_(g)) characteristics that were calculated.

FIG. 50 shows ideal I_(d)-V_(g) characteristics obtained by calculation and the actually measured I_(d)-V_(g) characteristics of the transistor when a source voltage V_(s) is 0 V and a drain voltage V_(d) is 0.1 V. Note that only values more than or equal to 1×10⁻¹³ A at which drain current I_(d) can be easily measured were plotted among the measurement results of the transistor.

A change of the drain current I_(d) with respect to the gate voltage V_(g) is more gradual in the actually measured I_(d)-V_(g) characteristics than in the ideal I_(d)-V_(g) characteristics obtained by calculation. This is probably because an electron is trapped by a shallow interface state positioned near energy at the conduction band minimum (represented as Ec). In this measurement, the density of interface states N_(it) can be estimated more accurately in consideration of the number of electrons (per unit area and unit energy) trapped by shallow interface states, N_(trap), with use of the Fermi distribution function.

First, a method for evaluating the number of electrons trapped by interface trap states, N_(trap), by using schematic I_(d)-V_(g) characteristics illustrated in FIG. 51 is described. The dashed line indicates ideal I_(d)-V_(g) characteristics without trap state which are obtained by the calculation. On the dashed line, a change in gate voltage V_(g) when the drain current changes from I_(d)1 to I_(d)2 is represented by ΔV_(id). The solid line indicates the actually measured I_(d)-V_(g) characteristics. On the solid line, a change in gate voltage V_(g) when the drain current changes from I_(d)1 to I_(d)2 is represented by ΔV_(ex). The potential at the target interface when the drain current is I_(d)1, the potential at the target interface when the drain current is I_(d)2, and the amount of change are represented by ϕ_(it1), ϕ_(it2), and Δϕ_(it), respectively.

The slope of the actually measured values is smaller than that of the calculated values in FIG. 51 , which indicates that ΔV_(ex) is always larger than ΔV_(id). Here, a difference between ΔV_(ex) and ΔV_(id) corresponds to a potential difference that is needed for trapping of an electron in a shallow interface state. Therefore, ΔQ_(trap) which is the amount of change in charge due to trapped electrons can be expressed by the following formula (6).

[Formula 6]

ΔQ _(trap) =−C _(tg)(ΔV _(ex) −ΔV _(id))  (6)

C_(tg) is combined capacitance of an insulator and a semiconductor per unit area. In addition, ΔQ_(trap) can be expressed by the formula (7) by using the number of trapped electrons N_(trap) (per unit area and per unit energy). Note that q represents elementary charge.

[Formula 7]

ΔQ _(trap) =−qN _(trap)Δϕ_(it)  (7)

Simultaneously solving the formulae (6) and (7) gives the formula (8).

[Formula 8]

−C _(tg)(ΔV _(ex) −ΔV _(id))=−qN _(trap)Δϕ_(it)  (8)

Then, taking the limit zero of Δϕ_(it) in the formula (8) gives the formula (9).

$\begin{matrix} \left\lbrack {{Formula}9} \right\rbrack &  \\ {N_{trap} = {{\frac{C_{tg}}{q}{\lim\limits_{{\Delta\phi_{it}}\rightarrow 0}\left( {\frac{\Delta V_{ex}}{{\Delta\phi}_{it}} - \frac{\Delta V_{id}}{{\Delta\phi}_{it}}} \right)}} = {C_{tg}\left( {\frac{\partial V_{ex}}{\partial\phi_{it}} - \frac{\partial V_{id}}{\partial\phi_{it}}} \right)}}} & (9) \end{matrix}$

In other words, the number of electrons trapped by an interface, N_(trap), can be estimated by using the ideal I_(d)-V_(g) characteristics, the actually measured I_(d)-V_(g) characteristics, and the formula (9). Note that the relationship between the drain current and the potential at the interface can be obtained by the above calculations.

The relationship between the number of electrons N_(trap) per unit area and per unit energy and the density of interface states N_(it) is expressed by the formula (10).

$\begin{matrix} \left\lbrack {{Formula}10} \right\rbrack &  \\ {N_{trap} = {\frac{\partial}{\partial\phi_{it}}{\int_{- \infty}^{\infty}{{N_{it}(E)}{f(E)}dE}}}} & (10) \end{matrix}$

Here, f(E) is Fermi distribution function. The N_(trap) obtained from the formula (9) is fitted with the formula (10) to determine N_(it). The conduction characteristics including I_(d)<0.1 pA can be obtained by the device simulator to which the N_(it) is set.

The actually measured I_(d)-V_(g) characteristics in FIG. 50 are applied to the formula (9) and the results of extracting N_(trap) are plotted as white circles in FIG. 52 . The vertical axis in FIG. 52 represents Fermi energy Ef at the conduction band minimum Ec of a semiconductor. The horizontal axis in FIG. 52 represents the density of states. The maximum value is positioned on the dashed line just under Ec. When tail distribution of the formula (11) is assumed as N_(it) of the formula (10), N_(trap) can be fitted well like the dashed line in FIG. 52 . As a result, the trap density at an end of the conduction band N_(ta)=1.67×10¹³ cm⁻² eV and the characteristic decay energy W_(ta)=0.105 eV are obtained as the fitting parameters.

$\begin{matrix} \left\lbrack {{Formula}11} \right\rbrack &  \\ {{N_{it}(E)} = {N_{ta}{\exp\left\lbrack \frac{E - E_{c}}{W_{ta}} \right\rbrack}}} & (11) \end{matrix}$

FIG. 53(A) and FIG. 53(B) show the inverse calculation results of I_(d)-V_(g) characteristics by feeding back the obtained fitting curve of interface state to the calculation using the device simulator. FIG. 53(A) shows the calculated I_(d)-V_(g) characteristics when the drain voltage V_(d) is 0.1 V and 1.8V and the actually measured I_(d)-V_(g) characteristics when the drain voltage V_(d) is 0.1 V and 1.8V. FIG. 53(B) is a graph in which the drain current I_(d) is a logarithm in FIG. 53(A).

The curve obtained by the calculation substantially matches with the plot of the actually measured values, which suggests that the calculated values and the measured values are highly reproducible. Thus, the above method is quite appropriate as a method for calculating the density of shallow defect states.

[Measurement Results of Density of Shallow Defect States]

Next, the density of shallow defect states of Sample 6A, Sample 6B, Sample 6C, Sample 6D, Sample 6E, Sample 6F, Sample 6G, Sample 6H, and Sample 6J were measured by comparing measured electrical characteristics with ideal calculation values according to the above-described method.

FIG. 54 shows calculated average density of shallow defect states of Sample 6A, Sample 6B, Sample 6C, Sample 6D, Sample 6E, Sample 6F, Sample 6G, Sample 6H, and Sample 6J.

As shown in FIG. 54 , the sample formed at a lower oxygen flow rate ratio in film formation of the metal oxide 108 or a lower temperature in film formation of the metal oxide 108 has a lower peak density of shallow defect states.

As described above, Sample 6A to Sample 6J were found to be transistors each including a metal oxide film with a low density of defect states. It is presumed that the oxygen-transmitting property is improved because the metal oxide film is formed at a low temperature and a low oxygen flow rate ratio, and that the amount of diffused oxygen in the fabrication process of the transistor is increased, whereby the amount of defects such as oxygen vacancies in the metal oxide film and at the interface between the metal oxide film and the insulating film is reduced.

At least part of this example can be implemented in combination with any of the embodiments and the other examples described in this specification as appropriate.

Example 7

In this example, the transistor 150 including the metal oxide 108 of one embodiment of the present invention was fabricated and the density of defect states was measured. In this example, nine transistors, i.e., Sample 7A, Sample 7B, Sample 7C, Sample 7D, Sample 7E, Sample 7F, Sample 7G, Sample 7H, and Sample 7J, were fabricated as the transistor 150 including the metal oxide 108.

<Structure of Samples and Fabrication Method Thereof>

Sample 7A to Sample 7J relating to one embodiment of the present invention will be described below. As Sample 7A to Sample 7J, the transistors 150 having the structure illustrated in FIG. 7 were fabricated by the fabrication method described in Embodiment 2 with reference to FIG. 9 to FIG. 11 .

Sample 7A to Sample 7J were fabricated at different temperatures and different oxygen flow rate ratios in film formation of the metal oxide 108. The metal oxide 108 was formed using a metal oxide target (In:Ga:Zn=4:2:4.1 [atomic ratio]). The temperatures and the oxygen flow rate ratios in film formation of the metal oxides of Sample 7A to Sample 7J are shown in the following table.

TABLE 7 O₂ Formation Flow rate [sccm] ratio temperature O₂ Ar [%] [° C.] Sample 7A 30 270 10 R.T. Sample 7B 90 210 30 R.T. Sample 7C 300 0 100 R.T. Sample 7D 30 270 10 130 Sample 7E 90 210 30 130 Sample 7F 300 0 100 130 Sample 7G 30 270 10 170 Sample 7H 90 210 30 170 Sample 7J 300 0 100 170

The samples were fabricated by the fabrication method described in Embodiment 2.

The transistor 150 had a channel length of 2 μm and a channel width of 3 (hereinafter, also referred to as L/W=2/3 μm) or a channel length of 2 μm and a channel width of 50 μm (hereinafter, also referred to as L/W=2/50 μm).

<Measurement of Shallow Defect States Using Transistor Characteristics> [Measurement Method of Density of Shallow Defect States]

Shallow defect states of the metal oxide 108 was estimated from electrical characteristics of a transistor in which the metal oxide was used as a semiconductor. The calculation method was similar to that described in the above example. The density of interface states of the transistor was measured, and subthreshold leakage current was estimated in consideration of the density of interface states and the number of electrons trapped by the interface states, N_(trap).

[Measurement Results of Density of Shallow Defect States]

Next, the density of shallow defect states of Sample 7A, Sample 7B, Sample 7C, Sample 7D, Sample 7E, Sample 7F, Sample 7G, Sample 7H, and Sample 7J were measured by comparing measured electrical characteristics with ideal calculation values according to the above-described method.

FIG. 55 shows calculated average density of shallow defect states of Sample 7A, Sample 7B, Sample 7C, Sample 7D, Sample 7E, Sample 7F, Sample 7G, Sample 7H, and Sample 7J.

As shown in FIG. 55 , the sample formed at a lower oxygen flow rate ratio in film formation of the metal oxide 108 or a lower temperature in film formation of the metal oxide 108 has a lower peak density of shallow defect states.

As described above, Sample 7A to Sample 7J were found to be transistors each including a metal oxide film with a low density of defect states. It is presumed that the oxygen-transmitting property is improved because the metal oxide film is formed at a low temperature and a low oxygen flow rate ratio, and that the amount of diffused oxygen in the fabrication process of the transistor is increased, whereby the amount of defects such as oxygen vacancies in the metal oxide film and at the interface between the metal oxide film and the insulating film is reduced.

At least part of this example can be implemented in combination with any of the embodiments and the other examples described in this specification as appropriate.

Example 8

In this example, the transistor 150 including the metal oxide 108 of one embodiment of the present invention was fabricated and subjected to tests for electrical characteristics and reliability. In this example, a transistor of Sample 8A was fabricated as the transistor 150 including the metal oxide 108.

<Structure of Samples and Fabrication Method Thereof>

Sample 8A relating to one embodiment of the present invention will be described below. As Sample 8A, the transistor 150 having the structure illustrated in FIG. 7 was fabricated by the fabrication method described in Embodiment 2 with reference to FIG. 9 to FIG. 11 .

The temperature and the oxygen flow rate ratio in film formation of the metal oxide 108 of Sample 8A are shown in the following table.

TABLE 8 O₂ Formation Flow rate [sccm] ratio temperature O₂ Ar [%] [° C.] Sample 8A 0 300 0 R.T.

Sample 8A was fabricated by the fabrication method described in Embodiment 2. The metal oxide 108 was formed using a metal oxide target (In:Ga:Zn=5:1:7 [atomic ratio]).

The transistor 150 had a channel length of 3 μm and a channel width of 50 μm (hereinafter, also referred to as L/W=3/50 μm).

<I_(a)- V_(g) Characteristics of Transistor>

Next, I_(d)-V_(g) characteristics of the transistor (L/W=3/50 μm) in Sample 8A fabricated above were measured. As conditions for measuring the I_(d)-V_(g) characteristics of each transistor, a voltage applied to the conductive film 112 serving as a first gate electrode (hereinafter, the voltage is also referred to as gate voltage (V_(g))) and a voltage applied to the conductive film 106 serving as a second gate electrode (hereinafter, the voltage is also referred to as back gate voltage (V_(bg))) were changed from −10 V to +10 V in increments of 0.25 V. A voltage applied to the conductive film 120 a serving as a source electrode (the voltage is also referred to as source voltage (Vs)) was 0 V (comm), and a voltage applied to the conductive film 120 b serving as a drain electrode (the voltage is also referred to as drain voltage (V_(d))) was 0.1 V and 20 V.

FIG. 56 shows the results of I_(d)-V_(g) characteristics and field-effect mobilities of Sample 8A. The solid line and the dashed-dotted line represent I_(d) at V_(d)=20 V and I_(d) at V_(d)=0.1 V, respectively. The dashed line represents field-effect mobility. In FIG. 56 , the first vertical axis represents I_(d) [A], the second vertical axis represents field-effect mobility (μFE) [cm²/Vs], and the horizontal axis represents V_(g) [V]. The field-effect mobility was calculated from the value measured at V_(d)=20 V.

Note that in FIG. 56 , measurement was performed with the upper limit of I_(d) in the measurement set to 1 mA. In FIG. 56 , when V_(d) is 20 V, I_(d) exceeds this upper limit at V_(g)=7.5 V. For this reason, FIG. 56 shows the field-effect mobility in the range where V_(g) is lower than or equal to 7.5 V as the field-effect mobility estimated from such I_(d)-V_(g) characteristics.

As shown in FIG. 56 , the transistor of this example has favorable electrical characteristics. Here, Table 9 shows the characteristics of the transistor shown in FIG. 56 .

TABLE 9 S Ioff μFE(@Vg = μFE(max)/ μFE(max) Vth [V/ [A/ 2 V) μFE(@Vg = [cm²V⁻¹s⁻¹] [V] decade] cm²] [cm²V⁻¹s⁻¹] 2 V) 103 −0.1 0.12 <1 × 10⁻¹² 70 1.47

As described above, the field-effect mobility of the transistor of this example exceeds 100 cm²/Vs. This field-effect mobility is equivalent to that of a transistor including low-temperature polysilicon and means extraordinary characteristics for a transistor using the metal oxide 108.

As shown in Table 9, Sample 8A includes a first region where the maximum value of the field-effect mobility of the transistor at a gate voltage higher than 0 V and lower than or equal to 10 V is larger than or equal to 60 cm²/Vs and smaller than 150 cm²/Vs, a second region where the threshold voltage is higher than or equal to −1 V and lower than or equal to 1 V, a third region where the S value is smaller than 0.3 V/decade, and a fourth region where the off-state current is lower than 1×10⁻¹² A/cm², and μ_(FE)(max)/μ_(FE)(V_(g)=2 V) is larger than or equal to 1 and smaller than 2 where μ_(FE)(max) represents the maximum value of the field-effect mobility of the transistor and μ_(FE)(V_(g)=2 V) represents the value of the field-effect mobility of the transistor at a gate voltage of 2 V.

The characteristics of the transistor can be obtained with the use of the metal oxide 108 described above. A transistor including the metal oxide 108 in its semiconductor layer can have both high carrier mobility and excellent switching characteristics.

At least part of this example can be implemented in combination with any of the embodiments and the other examples described in this specification as appropriate.

REFERENCE NUMERALS

-   001 region -   002 region -   100 transistor -   102 substrate -   104 insulating film -   106 conductive film -   108 metal oxide -   108 a metal oxide -   108 n region -   110 insulating film -   110_0 insulating film -   112 conductive film -   112_0 conductive film -   112_1 conductive film -   112_2 conductive film -   116 insulating film -   118 insulating film -   120 a conductive film -   120 b conductive film -   122 insulating film -   140 mask -   141 a opening -   141 b opening -   143 opening -   150 transistor -   160 transistor -   300A transistor -   300B transistor -   300C transistor -   300D transistor -   302 substrate -   304 conductive film -   306 insulating film -   307 insulating film -   308 metal oxide -   312 a conductive film -   312 b conductive film -   314 insulating film -   316 insulating film -   318 insulating film -   320 a conductive film -   320 b conductive film -   341 a opening -   341 b opening -   342 a opening -   342 b opening -   342 c opening -   600 display panel -   601 transistor -   604 connection portion -   605 transistor -   606 transistor -   607 connection portion -   612 liquid crystal layer -   613 conductive film -   617 insulating film -   620 insulating film -   621 insulating film -   623 conductive film -   631 coloring layer -   632 light-blocking film -   633 a alignment film -   633 b alignment film -   634 coloring layer -   635 conductive film -   640 liquid crystal element -   641 adhesive layer -   642 adhesive layer -   643 conductive film -   644 EL layer -   645 a conductive film -   645 b conductive film -   646 insulating film -   647 insulating film -   648 conductive film -   649 connection layer -   651 substrate -   652 conductive film -   653 semiconductor film -   654 conductive film -   655 opening -   656 polarizing plate -   659 circuit -   660 light-emitting element -   661 substrate -   662 display portion -   663 conductive film -   666 wiring -   672 FPC -   673 IC -   681 insulating film -   682 insulating film -   683 insulating film -   684 insulating film -   685 insulating film -   686 connector -   687 connector -   700 model -   702 local structure -   704 local structure -   706 local structure -   708 local structure -   710 local structure -   712 local structure -   901 region -   902 region -   903 region -   904 region -   905 region -   906 region -   907 region -   908 region -   909 region -   910 region -   911 region -   912 region -   913 region -   914 region -   915 region -   921 region -   922 region -   923 region -   924 region -   925 region -   926 region -   927 region -   928 region -   929 region -   930 region -   931 region -   932 region -   933 region -   934 region -   935 region 

What is claimed is:
 1. A composite oxide comprising a first region and a second region, wherein the composite oxide comprises a single-layer structure, wherein the first region comprises In, Zn and an element M1 (the element M1 is one or more of Al, Ga, Si, B, Y, Ti, Fe, Ni, Ge, Zr, Mo, La, Ce, Nd, Hf, Ta, W, Mg, V, Be, and Cu), wherein the second region comprises In, Zn, and an element M2 (the element M2 is one or more of Al, Ga, Si, B, Y, Ti, Fe, Ni, Ge, Zr, Mo, La, Ce, Nd, Hf, Ta, W, Mg, V, Be, and Cu), wherein a proportion of the element M1 to In, Zn, and the element M1 in the first region is less than a proportion of the element M2 to In, Zn, and the element M2 in the second region, wherein a proportion of In to In, Zn, and the element M1 in the first region is more than a proportion of In to In, Zn, and the element M2 in the second region, and wherein, when an analysis of the composite oxide by X-ray diffraction (thin film method) is performed, a diffraction pattern result in the X-ray diffraction has a peak whose shape is asymmetric with an angle at which a maximum intensity of the peak in X-ray diffraction is detected as a symmetry axis.
 2. The composite oxide according to claim 1, wherein the maximum intensity of the peak is detected between 2θ=30° and 2θ=35°.
 3. The composite oxide according to claim 1, wherein the element M1 and the element M2 are Ga.
 4. A transistor comprising: the composite oxide according to claim 1; and a gate, a source, and a drain, wherein the composite oxide is used in a channel region in the transistor.
 5. The composite oxide according to claim 1, further comprising a region including a nanocrystal and a crystalline region whose c-axis is aligned.
 6. The composite oxide according to claim 1, wherein the first region or the second region comprises a nanocrystal.
 7. The composite oxide according to claim 1, wherein the first region or the second region comprises a particle whose size is greater than or equal to 0.5 nm and less than or equal to 10 nm.
 8. The composite oxide according to claim 1, wherein the first region or the second region is not in an amorphous state, and comprises a particle whose size is greater than or equal to 0.5 nm and less than or equal to 10 nm.
 9. The composite oxide according to claim 1, wherein a plurality of spots are observed in a ring-shaped region in an electron diffraction pattern image of a part of the composite oxide.
 10. The transistor according to claim 4, wherein the transistor is provided in a pixel.
 11. The transistor according to claim 4, wherein the transistor is provided in a driver.
 12. The transistor according to claim 4, wherein the transistor is provided in a gate driver. 